Cross-copolymerized olefin/aromatic vinyl compound/diene copolymer and process for its production

ABSTRACT

A highly uniform vinyl compound polymer-cross-copolymerized olefin/styrene/diene copolymer excellent in processability, mechanical properties, high temperature properties, compatibility and transparency, and its composition and a process for its production, are provided. This copolymer is a crossed polymer obtained by cross-copolymerizing an olefin/styrene/diene copolymer having a styrene content of from 0.03 mol % to 96 mol %, a diene content of from 0.0001 mol % to 3 mol % and the rest being an olefin, with an olefin/aromatic vinyl compound copolymer.

This is a continuation-in-part application of the application Ser. No.09/831,358 having a filing date of May 14, 2001.

BACKGROUND OF THE INVENTION

1. Field of the Invention

The present invention relates to a novel cross-copolymerizedolefin/aromatic vinyl compound/diene copolymer (hereinafter sometimesabbreviated as a cross-copolymer) and its composition, and furtherprocesses for their production.

2. Discussion of Background

Ethylene/aromatic Vinyl Compound (styrene) Copolymers

Some ethylene/aromatic vinyl compound (styrene) random copolymersobtainable by means of a so-called uniform type Ziegler-Natta catalystsystem comprising a transition metal catalyst component and an organicaluminum compound, and processes for their production, are known.

JP-A-3-163088 and JP-A-7-53618 disclose ethylene/styrene copolymershaving a styrene content of at most 50 mol % and containing no normal(i.e. head-to-tail) styrene chain, so-called pseudo-random copolymers,obtainable by means of a complex having a so-called constrainedgeometric structure.

JP-A-6-49132 and Polymer Preprints, Japan, 42, 2292 (1993) discloseprocesses for producing similar ethylene/styrene copolymers having anaromatic vinyl compound content of at most 50 mol % and containing nonormal aromatic vinyl compound chain, i.e. pseudo-random copolymers, bymeans of a catalyst comprising a crosslinked metallocene type Zr complexand a cocatalyst. These copolymers have no stereoregularity derived fromaromatic vinyl compound units.

Further, recently, it has been reported to produce an ethylene/aromaticvinyl, compound copolymer having a stereoregularity of alternatingcopolymerization type by means of a certain specific crosslinkedbisindenyl type Zr complex i.e. a racemic[ethylenebis(indenyl)zirconiumdichloride] under an extremely low temperature (−25° C.) condition.(Macromol. Chem., Rapid Commun., 17, 745 (1996).) However, with thecopolymer obtainable by this complex, the molecular weight is not yetpractically sufficient, and the compositional distribution is alsolarge.

Further, JP-A-9-309925 and JP-A-11-130808 disclose novelethylene/styrene copolymers which respectively have styrene contents offrom 1 to 55 mol % and from 1 to 99 mol % and which haveethylene/styrene alternating structures and isotactic stereoregularityin their styrene chain structures and further have head-to-tail styrenechain structures, with the alternating degrees (λ values in thisspecification) of the copolymers being at most 70. Further, thesecopolymers have high transparency.

The physical properties of various ethylene/styrene random copolymersmentioned above, are strongly influenced by the compositions (thestyrene contents) when their molecular weights are sufficiently high.Namely, a copolymer having a relatively low styrene content at a levelof at most 20 mol %, has crystallizability based on the polyethylenechains, whereby it may have heat resistance at a level of from 80° C. to120° C. and further has high mechanical properties. However, if thestyrene content becomes higher, the crystallizability derived form thepolyethylene chains tends to decrease or diminish, and the heatresistance and mechanical properties tend to decrease. When there isstereoregularity in ethylene/styrene alternating structures, andrelatively many such alternating structures are contained, thecrystallizability derived from such alternating structures will appear,but there may sometimes be a problem with respect to the crystallinityor the crystallization rate. In a copolymer having a high styrenecontent of at least 60 mol %, many isotactic styrene chain structuresare contained, but isotactic styrene chains have a low crystallizationrate, whereby it may lack in practical applicability as a heat resistantresin.

On the other hand, a copolymer having a low styrene content is excellentalso in cold resistance (embrittle temperature) at a level of −60° C.However, as the styrene content increases, the cold resistance tends, todeteriorate, and in the vicinity of 30 mol %, it will be about −10° C.,and in the vicinity of 50 mol %, it will be about room temperature.

A copolymer having a styrene content of from about 15 to 50 mol %, has afeeling, flexibility and stress relaxation property similar to polyvinylchlorides and is useful as a substitute for polyvinyl chlorides.Further, it is excellent in vibration-damping properties andsoundproofing properties. However, its heat resistance and coldresistance are poor, whereby it is hardly useful by itself.

When used as a stretch film, a copolymer having a styrene content offrom about 30 to 50 mol % shows slow elongation recovery propertiessimilar to a polyvinyl chloride stretch film at room temperature, but ittends to be too stiff under a refrigerating or freezing condition.Further, when it is attempted to produce this film by inflation moldingor extrusion molding with a T-die, the film itself has a high self-tackproperty, and during winding, the film tends to adhere to itself. Aself-tack property to some extent is effective for a substitute for apolyvinyl chloride film, especially as a stretch film for foodpackaging, but it can hardly be compatible with film moldability.

An ethylene/styrene copolymer having a styrene content of at least 40mol % is excellent in printability and tinting property and has animproved compatibility with a styrene type resin. Especially, acopolymer having a styrene content of at most 20 mol % is inferior inprintability and tinting property, but is excellent in compatibilitywith a polyolefin type resin.

These random ethylene/styrene copolymers show remarkable changes in thephysical properties and compatibility depending upon the compositions asdescribed above, and they have had a problem that with a singlecomposition, various properties (such as heat resistance, coldresistance and stress relaxation property or flexibility) can not besatisfied at the same time.

In order to solve such a problem, it has been proposed to mixethylene/styrene copolymers having different compositions to obtain acomposition (JP-A-2000-129043, WO98/10018), to mix them with polyolefinsto obtain compositions (WO98/10015), or to crosslink them (U.S. Pat. No.5,869,591). However, ethylene/styrene copolymers substantially differentin their compositions have poor compatibility to one another, and theircompositions or compositions with polyolefins tend to be opaque, and themechanical properties may sometimes be impaired, whereby the applicationmay be limited. Further, in the case of crosslinking, there is a problemthat the secondary moldability or recycling property tends to be lost,or the production cost tends to increase.

Ethylene/α-olefin Copolymers

Ethylene/α-olefin copolymers, in which 1-hexene, 1-octene or the like isco-polymerized to ethylene, i.e. so-called LLDPE, are flexible andtransparent and have high strength, whereby they are widely used as e.g.films for general use, packaging materials or containers. However, as anature of polyolefin type resins, their printability and coatingproperties are low, and special treatment such as corona treatment willbe required for printing or coating. Further, they have poor affinitywith an aromatic vinyl compound polymer such as a polystyrene or a polarpolymer, and in order to obtain a composition with such a resin havinggood mechanical properties, it has been necessary to employ an expensivecompatibilizing agent additionally.

Common Graft Copolymers

As a method for obtaining a graft copolymer, a method has beenheretofore known wherein a graft copolymer of an olefin type polymer oran olefin/styrene type copolymer is obtained during the polymerizationor during the mold processing by a common known radical graft treatment.However, by this method, it has been difficult to obtain high graftefficiency, and the method is disadvantageous from the viewpoint ofcosts. Further, the obtainable graft copolymer usually has a problemthat it is non-uniform and partially gelled to be not melting, wherebythe moldability tends to be impaired. The graft copolymer thus obtained,usually has graft chains independently branched from the polymer mainchain, but when such copolymer is employed as a composition or acompatibilizing agent, the strength of the interface of the polymermicrostructure can not be said to be sufficient.

SUMMARY OF THE INVENTION

The present invention is firstly to solve the foregoing problems of theprior art and to provide a cross-copolymerized olefin/aromatic vinylcompound/diene copolymer which satisfies heat resistance and variousmechanical properties, processability, compatibility and transparency,and its composition and an industrially excellent process for producingsuch a cross-copolymer.

The present invention is secondly to provide as applications of thecross-copolymer of the present invention, various resin compositions ormolded products containing the cross-copolymer, which have theabove-mentioned problems of various resin compositions or moldedproducts solved or improved.

DISCLOSURE OF THE INVENTION

Cross-copolymerized Olefin/aromatic Vinyl Compound/diene Copolymer (across-copolymer)

In this specification, an aromatic vinyl compound content of a copolymerrepresents a content of units derived from an aromatic vinyl compoundmonomer, contained in the copolymer. An olefin content and a dienecontent likewise represent contents of the respective monomer units.

The cross-copolymer of the present invention is a cross-copolymerizedolefin/aromatic vinyl compound/diene copolymer characterized in that itis obtained by cross-copolymerizing an olefin/aromatic vinylcompound/diene copolymer having an aromatic vinyl compound content offrom 0.03 mol % to 96 mol %, a diene content of from 0.0001 mol % to 3mol % and the rest being an olefin, with an olefin/aromatic vinylcompound copolymer (which may contain a diene) having an aromatic vinylcompound content which is different by at least 5 mol %.

Further, the cross-copolymer of the present invention is a copolymer(which will be referred to as a cross-copolymerized olefin/aromaticvinyl compound/diene copolymer or simply as a cross-copolymer) obtainedby synthesizing an olefin/aromatic vinyl compound/diene copolymer havingan aromatic vinyl compound content of from 0.03 mol % to 96 mol %, adiene content of from 0.0001 mol % to 3 mol % and the rest being anolefin (main chain), followed by cross-copolymerizing an olefin/aromaticvinyl compound copolymer having an aromatic vinyl compound content offrom 0 mol % to 96 mol % and the rest being an olefin, preferably anaromatic vinyl compound content of from 0.03 mol % to 96 mol % and therest being an olefin, wherein the aromatic vinyl compound content isdifferent by at least 5 mol %.

Further, the cross-copolymer of the present invention is across-copolymerized olefin/aromatic vinyl compound/diene copolymercharacterized in that it is obtained, by using an olefin/aromatic vinylcompound/diene copolymer having an aromatic vinyl compound content offrom 0.03 mol % to 96 mol %, a diene content of from 0.0001 mol % to 3mol % and the rest being an olefin, and cross-copolymerizing it, whereinthe aromatic vinyl compound content is different by at least 2 mol % ascompared with the olefin/aromatic vinyl compound/diene copolymer priorto the cross-copolymerization.

Further, preferably, the cross-copolymer of the present invention is across-copolymerized olefin/aromatic vinyl compound/diene copolymercharacterized in that it is obtained by cross-copolymerizing anolefin/aromatic vinyl compound/diene copolymer having an aromatic vinylcompound content of from 0.03 mol % to 96 mol %, a diene content of from0.0001 mol % to 3 mol % and the rest being an olefin, with an olefin(co)polymer or an olefin/aromatic vinyl compound copolymer (which maycontain a diene), wherein the aromatic vinyl compound content isdifferent by at least 2 mol %, preferably at least 5 mol %, as comparedwith an olefin/aromatic vinyl compound/diene copolymer prior to thecross-copolymerization.

The cross-copolymer of the present invention may finally have acomposition such that the aromatic vinyl compound content is from 0.03mol % to 96 mol %, the diene content is from 0.0001 mol % to 3 mol %,and the rest being an olefin, preferably a composition such that thearomatic vinyl compound content is from 5 mol % to 96 mol %, the dienecontent is from 0.0001 mol % to 3 mol %, and the rest being an olefin.

The weight average molecular weight of the cross-copolymer of thepresent invention is at least 10,000, preferably at least 30,000,particularly preferably at least 60,000, and at most 1,000,000,preferably at most 500,000. The molecular weigh distribution (Mw/Mn) isnot particularly limited, but is usually at most 10, preferably at most7, most preferably at most 5, and at least 1.5.

Further, in the specification of the present invention, thecross-copolymer is a polymer which can directly be obtained by theprocess of the present invention.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a schematic view illustrating the cross-copolymer of thepresent invention.

FIG. 2 is a schematic view illustrating a conventional graftedcopolymer.

FIG. 3 is a graph showing the relation between the melting points andthe compositions of cross-copolymers of Examples 1 to 3 of the presentinvention and ethylene/styrene copolymers.

FIG. 4 is a graph showing the relation between the Vicat softeningpoints and the compositions of cross-copolymers of the presentinvention, ethylene/styrene copolymers and blends of ethylene/styrenecopolymers.

FIG. 5 shows an X-ray diffraction diagram and a multiple peak separationresults of a cross-copolymer of the present invention.

FIG. 6 is an X-ray diffraction diagram and a multiple peak separationresult of an ethylene/styrene copolymer.

FIG. 7 is a viscoelasticity spectrum of cross-copolymer (1-C).

FIG. 8 is a viscoelasticity spectrum of cross-copolymer (2-C).

FIG. 9 is a viscoelasticity spectrum of an ethylene/styrene copolymerhaving a styrene content of 11 mol %.

FIG. 10 is a graph showing the relation between the melting points andthe compositions of cross-copolymers of Examples 8 to 13 of the presentinvention and ethylene/styrene copolymers.

FIG. 11 is a transmission electron microscopic (TEM) photograph of across-copolymer.

FIG. 12 is a TEM photograph of an ethylene/styrene copolymer compositionof Comparative Example 7.

DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS

Further, the present invention is a cross-copolymer constitutedpreferably by the structure shown in FIG. 1 or comprising the structureshown in FIG. 1.

Namely, as shown in FIG. 1, it is a copolymer having mainly a structurein which a main chain olefin/aromatic vinyl compound/diene copolymer isbonded (cross-bonded or intersectingly bonded) with cross chains, at onepoint or plural points, via diene units. Such a cross-structure may berephrased as a star structure. Further, in the classification by thePOLY division of the American Chemical Society, it is called asegregated star copolymer (Polymer Preprints, 1998, March). In thedescription of the present invention, the olefin/aromatic vinyl compoundcopolymer or olefin (co)polymer cross-bonded to the main chainolefin/aromatic vinyl compound/diene copolymer will be referred to as across chain.

Whereas as shown in FIG. 2, a graft copolymer known to those skilled inthe art is a copolymer having mainly polymer chains branched from onepoint or plural points of the main chain.

With a structure such that a polymer main chain is cross-bonded(intersectingly bonded) with other polymer chains (which may be calledalso as a star structure), when it is employed as a composition orcompatibilizing agent, it is usually believed to show superior strengthof the interface of the polymer microstructure and present highmechanical properties, as compared with a grafted structure.

Preferably, the cross-copolymer of the present invention hascharacteristics such that at least one melting point by DSC is observedat a level of from 80° C. to 140° C., preferably from 95° C. to 140° C.,and its heat of crystal fusion is at least 10 J/g and at most 150 J/g,preferably at least 20 J/g and at most 120 J/g. The crystal structure togive such heat of crystal fusion is preferably a crystal structure basedon an ethylene chain structure. This crystal structure can beascertained by a known method such as an X-ray diffraction method.

Further, the cross-copolymer of the present invention is across-copolymerized olefin/aromatic vinyl compound/diene copolymer,characterized in that it has an aromatic vinyl compound content of from5 mol % to 50 mol %, a diene content of from 0.0001 mol % to 3 mol % andthe rest being ethylene or at least two types of olefins includingethylene, and it has a crystal structure derived from an ethylene chainstructure, wherein the aromatic vinyl compound content and at least oneof the melting point such that the heat of crystal fusion as measured byDSC is at least 10 J/g and at most 150 J/g, satisfies the followingrelation:(5≦St≦15)−3·St+125≦Tm≦140(15<St≦50)80<Tm≦140where Tm is the melting point (° C.) such that the heat of crystalfusion is at least 10 J/g and at most 150 J/g, and St is the aromaticvinyl compound content (mol %).

Further preferably, the cross-copolymer of the present invention is across-copolymerized olefin/aromatic vinyl compound/diene copolymer,characterized in that it has an aromatic vinyl compound content of from5 mol % to 15 mol %, a diene content of from 0.0001 mol % to 3 mol % andthe rest being ethylene or at least two types of olefins includingethylene, wherein the aromatic vinyl compound content and the meltingpoint such that the heat of crystal fusion as measured by DSC is atleast 10 J/g and at most 150 J/g, satisfy the following relation:(5≦St≦10)−3·St+125≦Tm≦140(10<St≦15)95≦Tm≦140where Tm is the melting point (° C.) such that the heat of crystalfusion is at least 10 J/g and at most 150 J/g, and St is the aromaticvinyl compound content (mol %).

Further preferably, it is a cross-copolymerized olefin/aromatic vinylcompound/diene copolymer which has a single melting point as observed byDSC and the melting point of which satisfies the above-mentionedrelation.

Further, the cross-copolymer of the present invention is across-copolymerized olefin/aromatic vinyl compound/diene copolymer,characterized in that it has an aromatic vinyl compound content of from5 mol % to 20 mol %, a diene content of from 0.0001 mol % to 3 mol % andthe rest being ethylene of at least two types of olefins includingethylene, wherein the aromatic vinyl compound content, and the Vicatsoftening point satisfy the following relation:(5≦St≦20)−3·St+120≦T vicat≦140where T vicat is the Vicat softening point (° C.), and St is thearomatic vinyl compound content (mol %).

Further preferably, it is a cross-copolymerized olefin/aromatic vinylcompound/diene copolymer, characterized in that it has an aromatic vinylcompound content of from 5 mol % to 15 mol %, a diene content of from0.0001 mol % to 3 mol % and the rest being ethylene or at least twotypes of olefins including ethylene, wherein the aromatic vinyl compoundcontent and the Vicat softening point satisfy the following relation:(5≦St≦15) −3·St+120≦T vicat≦140where T vicat is the Vicat softening point (° C.), and St is thearomatic vinyl compound content (mol %).

Among cross-copolymers of the present invention, a cross-copolymerizedethylene/styrene/divinylbenzene copolymer can have at least one glasstransition point within a range of from −30° C. to −15° C. The glasstransition point is a glass transition point obtained by a tangentmethod (on set method) in the DSC measurement.

In a molded sheet product of 1 mm, the cross-copolymerizedolefin/aromatic vinyl compound/diene copolymer of the present invention,may have a haze of at most 30%, preferably at most 20%.

In a heat molded product of 1 mm, the cross-copolymerizedolefin/aromatic vinyl compound/diene copolymer of the present inventionmay have a total light transmittance of at least 70%, preferably atleast 80%.

Further, the present invention is a cross-copolymerized olefin/aromaticvinyl compound/diene compound excellent in processability, of which MFRas measured under a load of 5 kg at 200° C. is at least 0.02 g/10 min.,preferably at least 0.2 g/10 min. and at most 100 g/10 min., morepreferably MFR as measured under a load of 5 kg at 230° C. is at least1.0 g/10 min. and at most 50 g/10 min.

Further, the present invention is a cross-copolymerized olefin/aromaticvinyl compound/diene copolymer containing a small gel content orsubstantially no gel content, whereby the boiling xylene insoluble (thegel content) obtained by ASTM D-2765-84 is less than 10 weight %,preferably less than 1 weight %, most preferably, less than 0.1 weight%, of the entirety.

The present invention is preferably a cross-copolymerizedolefin/aromatic vinyl compound/diene copolymer, wherein the olefin isethylene or at least two types of olefins including ethylene.

Further, the cross-copolymer of the present invention is a copolymerwhich can be obtained by the following process.

The cross-copolymer of the present invention includes not only a conceptrepresenting the cross-copolymer itself but also a concept of acomposition containing the cross-copolymer and an olefin/aromatic vinylcompound copolymer not-crossed, which is obtainable in the firstpolymerization step and the second or subsequent polymerization step(which may sometimes be hereinafter referred to as a secondpolymerization step) at an optional ratio. Such a composition containinga cross-copolymer can be obtained by the process of the presentinvention.

The cross-copolymer of the present invention has different contents ofvinyl aromatic compound in the main chain and in the cross chains, sothat if it contains olefin/aromatic vinyl compound copolymers withdifferent compositions (aromatic vinyl compound contents), which areobtainable in the respective polymerization steps, it is believed tohave a function as a compatibilizing agent for them. Therefore, thecross-copolymer obtainable by the process of the present invention, isconsidered to have excellent mechanical properties, high heatresistance, transparency and processability, as compared with usualolefin/aromatic vinyl compound copolymers.

Further, the present invention provides an economically excellentprocess for producing a cross-copolymerized olefin/aromatic vinylcompound/diene copolymer and provides a cross-copolymerizedolefin/aromatic vinyl compound/diene copolymer thereby obtainable. Sucha cross-copolymer is very useful in a wide range of applications.

Process for Producing a Cross-copolymerized Olefin/aromatic VinylCompound/diene Copolymer

The present invention is a cross-copolymerized olefin/aromatic vinylcompound/diene copolymer (a cross-copolymer) which can be obtained bythe following process. Further, the process for producing across-copolymer is capable of producing a cross-copolymer which isuniform and which has good processability and excellent transparency andmechanical properties with efficiency and economical feasibilitysuitable for industrial application.

Namely, the present invention is a process for producing across-copolymer, which comprises, as a first polymerization step (a mainchain polymerization step), carrying out copolymerization of an aromaticvinyl compound monomer, an olefin monomer and a diene monomer by meansof a coordination polymerization catalyst to synthesize anolefin/aromatic vinyl compound/diene copolymer, and then, as a secondpolymerization step (a crossing step), cross-copolymerizing anolefin/aromatic vinyl compound copolymer using such a copolymer, anolefin, an aromatic vinyl compound monomer and a coordinationpolymerization catalyst. This process is a process employing at leasttwo polymerization steps comprising the above first polymerization step(the main polymerization step) and the second polymerization step (thecrossing step).

It is necessary that the aromatic vinyl compound content of theolefin/aromatic vinyl compound/diene copolymer to be polymerized in thefirst polymerization step (the main chain polymerization step) and theaverage aromatic vinyl compound content of an olefin/aromatic vinylcompound copolymer to be polymerized in the second or subsequentpolymerization step (which may sometimes be hereinafter referred to as asecond polymerization step) (when the polymerization solution obtainedin the first polymerization step, is used itself in the secondpolymerization step, the polymer thereby obtainable contains a smallamount of a residual diene copolymerized) are different by at least 5mol %, preferably at least 10 mol %, most preferably at least 15 mol %.The aromatic vinyl compound content of an olefin/aromatic vinyl compoundcopolymer to be polymerized in the second or subsequent polymerizationstep (the crossing step) may be 0% in an extreme case. In such a case,an olefin polymer containing no aromatic vinyl compound will be crosschains.

Further, it is necessary that the aromatic vinyl compound content of theolefin/aromatic vinyl compound/diene copolymer in the firstpolymerization step and the aromatic vinyl compound content of thefinally obtainable cross-copolymerized olefin/aromatic vinylcompound/diene copolymer are different by at least 2 mol %, preferablyat least 5 mol %, more preferably at least 10 mol %.

First Polymerization Step (main chain polymerization step)

The olefin/aromatic vinyl compound/diene copolymer to be used in thepresent invention, can be obtained by copolymerizing an aromatic vinylcompound monomer, an olefin monomer and a diene monomer in the presenceof a single site coordination polymerization catalyst.

The olefin to be used in the present invention may, for example, beethylene or a C₃₋₂₀ α-olefin, such as propylene, 1-butene, 1-hexene,4-methyl-1-pentene or 1-octene, or a cyclic olefin such as cyclopenteneor norbornene. Preferably, a mixture of ethylene with an α-olefin suchas propylene, 1-butene, 1-hexene or 1-octene, an α-olefin such aspropylene, or ethylene, is employed. More preferably ethylene or amixture of ethylene with an α-olefin, is employed. Particularlypreferably, ethylene is employed.

As the aromatic vinyl compound to be used in the present invention,styrene is preferably employed, but it is possible to employ otheraromatic vinyl compound, such as p-chlorostyrene, p-tert-butylstyrene,vinyl naphthalene, p-methylstyrene, vinyl naphthalene or vinylanthracene. Further, a mixture of such compounds may be employed.

Further, as the diene to be used in the present invention, acoordination-polymerizable diene may be employed. Preferably,1,4-hexadiene, 1,5-hexadiene, ethylidenenorbornene, dicyclopentadiene,norbornadiene, 4-vinyl-1-cyclohexene, 3-vinyl-1-cyclohexene,2-vinyl-1-cyclohexene-, o-divinylbenzene, p-divinylbenzene,m-divinylbenzene, or a mixture of them, may be mentioned. Further, it ispossible to employ a diene wherein a plurality of double bonds (vinylgroups) are bonded via a C₆₋₃₀ hydrocarbon group containing a single orplural aromatic vinyl ring structures. Further, dienes disclosed inJP-A-6-136060 and JP-A-11-124420 can also be employed in the presentinvention. Preferred is a diene wherein one of double bonds (vinylgroups) is used for coordination polymerization so that remaining doublebonds in a polymerized state are coordination-polymerizable. Morepreferably, one of o-, p- and m-divinylbenzenes, or a mixture thereof,is suitably employed. Most preferably, m-divinylbenzene having an isomerpurity of at least 80 weight %, preferably at least 90 weight %, isemployed.

In the present invention, the amount of the diene to be used in the mainchain polymerization step is from 1/50,000 to 1/100, preferably from1/20,000 to 1/400, of the amount of styrene to be used, in a molarratio. If the main chain polymerization step is carried out at a dieneconcentration higher than this, many crosslinking structures of polymerwill be formed during the polymerization, whereby gelation or the likewill take place, or the processability or physical properties of thecross-copolymer finally obtainable via the crossing step, tend todeteriorate, such being undesirable. Further, if the main chainpolymerization step is carried out at a diene concentration higher thanthis, the residual diene concentration in the polymerization solutiontends to be high, and if such a polymer solution is used for thecrossing step as it is, many crosslinking structures tend to form,whereby the obtained cross-copolymer tends to be likewise poor in theprocessability or physical properties.

In order to obtain a cross-copolymer excellent particularly in softness,the olefin/aromatic vinyl compound/diene copolymer polymerized in thefirst polymerization step (the main chain polymerization step),preferably has a composition wherein the aromatic vinyl compound contentis at least about 15 mol % and at most 50 mol %, the diene content is atleast 0.001 mol % and less than 0.5 mol %, and the rest is an olefin.Particularly, in order to obtain a cross-copolymer having thecharacteristics of a soft polyvinyl chloride resin (a feeling such assoftness, a tan δ component in the vicinity of room temperature in theviscoelasticity spectrum), the aromatic vinyl compound is particularlypreferably styrene, and in such a case, an olefin/aromatic vinylcompound/diene copolymer having a styrene content of from about 20 mol %to 50 mol %, a diene content of from 0.001 mol % to less than 0.5 mol %and the rest being an olefin, is employed.

Further, in order to obtain a cross-copolymer having both softness andcold resistance, the olefin/aromatic vinyl compound/diene copolymerpolymerized in the first polymerization step (the main chainpolymerization step), preferably has a composition wherein the aromaticvinyl compound content is at least 10 mol % and at most 30 mol %, thediene content is at least 0.001 mol % and less than 0.5 mol %, and therest is an olefin.

Further, the diene content of the olefin/aromatic vinyl compound/dienecopolymer obtained in the first polymerization step (the main chainpolymerization step) is at least 0.0001 mol % and at most 3 mol %,preferably at least 0.001 mol % and less than 0.5 mol %, most preferablyat least 0.01 mol % and less than 0.3 mol %. If the diene content in thecopolymer is higher, the processability of the cross-copolymer finallyobtainable via the second polymerization step (the crossing step) tendsto be poor, such being undesirable.

The single site coordination polymerization catalyst to be used in thefirst polymerization step (the main chain polymerization step) may, forexample, be a polymerization catalyst comprising a transition metalcompound and a cocatalyst i.e. a soluble Zieglar-Natta catalyst or atransition metal compound catalyst activated with methyl aluminoxane ora boron compound (a so-called metallocene catalyst or half metallocenecatalyst, a CGCT catalyst, etc.).

Specifically, polymerization catalysts disclosed in the followingliteratures and patents, can be employed.

For example, metallocene catalysts disclosed in U.S. Pat. No. 5,324,800,JP-A-7-37488, JP-A-6-49132, Polymer Preprints, Japan, 42, 2292 (1993),Macromol. Chem., Rapid Commun., 17, 745 (1996), JP-A-9-309925,EP0872492A2 and JP-A-6-184179.

Half metallocene catalysts disclosed in Makromol. Chem. 191, 2387(1990).

CGCT catalysts disclosed in JP-A-3-163088, JP-A-7-53618 and EP-A 416815.

Soluble Zieglar-Natta catalysts disclosed in JP-A-3-250007 and Stud.Surf. Sci. Catal., 517 (1990).

An olefin/aromatic vinyl compound/diene copolymer having a uniformcomposition with a diene uniformly contained in the polymer, is suitablyemployed to obtain a cross-copolymer of the present invention. However,it is difficult to obtain such a copolymer having a uniform compositionby Zieglar-Natta catalyst, and a single site coordination polymerizationcatalyst is preferably employed. The single site coordinationpolymerization catalyst is a polymerization catalyst comprising atransition metal compound and a cocatalyst, i.e. a polymerizationcatalyst comprising a transition metal compound catalyst activated withmethyl aluminoxane or a boron compound (a so-called metallocene catalystor half metallocene catalyst, a CGCT catalyst, etc.).

In the present invention, a single site coordination polymerizationcatalyst comprising one type of a transition metal compound and acocatalyst, is preferably employed.

In the present invention, the single site coordination polymerizationcatalyst to be most preferably employed, is a polymerization catalystcomprising a transition metal compound represented by the followinggeneral formula (1) and a cocatalyst.

When a polymerization catalyst comprising a transition metal compoundrepresented by the following general formula (1) and a cocatalyst, isemployed, a diene, particularly divinylbenzene, can be copolymerized toa polymer in high efficiency, whereby it is possible to substantiallyreduce the amount of the diene to be employed in the firstpolymerization step (the main chain polymerization step) and the amountof an unreacted diene remaining in the polymerization solution.

If the amount of the diene to be employed in the main chainpolymerization step is large, i.e. if the concentration is high,crosslinking of the polymer takes place substantially as the diene unitstructures serve as crosslinking points during the main chainpolymerization, whereby gelation or non-solubilization takes place, andthe cross-copolymer or the processability of the cross-copolymer tendsto deteriorate. Further, if the non-polymerized diene remainssubstantially in the polymerization solution obtained in the main chainpolymerization step, the crosslinking degree of cross chains will beremarkably high in the subsequent cross polymerization step, whereby theobtained crossed copolymer or the cross-copolymer will be insolubilizedor gelled to deteriorate the processability.

Further, when a polymerization catalyst comprising a transition metalcompound represented by the following general formula (1) and acocatalyst, is employed, it is possible to produce an olefin/aromaticvinyl compound/diene copolymer having a uniform composition with aremarkably high activity suitable for industrial application. Further, acopolymer having high transparency can be presented especially with acopolymer having an aromatic vinyl compound content of from 1 mol % to20 mol %. Further, with a composition having an aromatic vinyl compoundcontent of from 1 mol % to 96 mol %, an olefin/aromatic vinylcompound/diene copolymer excellent in mechanical properties, having anisotactic stereoregularity and a head-to-tail styrene chain structure,can be presented.

wherein A and B are independently a group selected from an unsubstitutedor substituted benzoindenyl group, an unsubstituted or substitutedcyclopentadienyl group, an unsubstituted or substituted indenyl group,or an unsubstituted or substituted fluorenyl group;

-   -   Y is a methylene group, a silylene group, an ethylene group, a        germilene group or a boron residue, which has bonds to A and B        and which further has hydrogen or a group containing a C₁₋₂₀        hydrocarbon (this group may have from 1 to 5 nitrogen, boron,        silicon, phosphorus, selenium, oxygen, fluorine, chlorine or        sulfur atoms), as a substituent, the substituents may be the        same or different from one another, and Y may have a cyclic        structure such as a cyclohexylidene group or a cyclopeontylidene        group;    -   each X is independently hydrogen, a halogen, a C₁₋₁₅ alkyl        group, a C₆₋₁₀ aryl group, a C₈₋₁₂ alkylaryl group, a silyl        group having a C₁₋₄ hydrocarbon substituent, a C₁₋₁₀ alkoxy        group, or an amide group having hydrogen or a C₁₋₂₂ hydrocarbon        substituent, and n is an integer of 0, 1 or 2; and    -   M is zirconium, hafnium or titanium,

Particularly preferred is a polymerization catalyst comprising atransition metal compound of the above general formula (1), wherein atleast one of A and B is an unsubstituted or substituted benzoindenylgroup or an unsubstituted or substituted indenyl group, and acocatalyst.

The unsubstituted or substituted benzoindenyl group can be representedby the following formulae Ka 3 to Ka 5. In the following chemicalformulae, each of R1b to R3b which are independent of one another, ishydrogen, a C₁₋₂₀ hydrocarbon group which may contain from 1 to 3nitrogen, boron, silicon, phosphorus, selenium, oxygen or sulfur atoms,preferably a C₁₋₂₀ alkyl group, a C6-10 aryl group or a C₇₋₂₀ alkylarylgroup, or a halogen atom, an OSiR₃ group, a SiR₃ group, a NR₂ group or aPR₂ group (each R represents a C₁₋₁₀ hydrocarbon group). Further,adjacent such groups may together form a single or plural 5- to10-membered aromatic or alicyclic rings.

Further, each of R1a to R3a which are independent of one another, ishydrogen, a C₁₋₂₀ hydrocarbon group which may contain from 1 to 3nitrogen, boron, silicon, phosphorus, selenium, oxygen or sulfur atoms,preferably a C₁₋₂₀ alkyl group, a C₆₋₁₀ aryl group or a C₇₋₂₀ alkylarylgroup, or a halogen atom, an OSiR₃ group, a SiR₃ group, NR₂ group or aPR₂ group (each R represents a C₁₋₁₀ hydrocarbon group), but ispreferably hydrogen.

The unsubstituted benzoindenyl group may, for example, be4,5-benzo-1-indenyl (another name: benzo(e)indenyl), 5,6-benzo-1-indenylor 6,7-benzo-1-indenyl, and the substituted benzoindenyl group, may, forexample, be α-acenaphtho-1-indenyl, 3-cyclopenta[c]phenanthryl, or1-cyclopenta[1]phenanthryl.

Particularly preferably, the unsubstituted benzoindenyl group is4,5-benzo-1-indenyl (another name: benzo(e)indenyl), and the substitutedbenzoindenyl may, for example, be α-acenaphtho-1-indenyl,3-cyclopenta[c]phenanthryl or 1-cyclopenta[1]phenanthryl.

The unsubstituted or substituted indenyl group, the unsubstituted orsubstituted fluorenyl group, or the unsubstituted or substitutedcyclopentadienyl group may be represented by the formulae Ka 6 to Ka 8.

Each of R4b and R6 which are independent of each other is hydrogen, aC₁₋₂₀ hydrocarbon group which may contain from 1 to 3 nitrogen, boron,silicon, phosphorus, selenium, oxygen or sulfur atoms, preferably aC₁₋₂₀ alkyl group, a C₆₋₁₀ aryl group or a C₇₋₂₀ alkylaryl group, or ahalogen atom, an OSiR₃ group, a SiR₃ group, a NR₂ group or a PR₂ group(each R represents a C₁₋₁₀ hydrocarbon group). Further, adjacent suchgroups may together form a single or plural 5- to 10-membered (exceptfor 6-membered) aromatic or alicyclic rings. However, preferred ishydrogen.

Each R5 is independently hydrogen, a C₁₋₂₀ hydrocarbon group which maycontain from 1 to 3 nitrogen, boron, silicon, phosphorus, selenium,oxygen or sulfur atoms, preferably a C₁₋₂₀ alkyl group, a C₆₋₁₀ arylgroup, or a C₇₋₂₀ alkylaryl group, or a halogen atom, an OSiR₃ group, aSiR₃ group, a NR₂ group or a PR₂ group (each R represents a C₁₋₁₀hydrocarbon group). Further, adjacent such groups may together form asingle or plural 5- to 10-membered aromatic or alicyclic rings. However,preferred is hydrogen.

Further, R₄a is independently hydrogen, a C₁₋₂₀ hydrocarbon group whichmay contain from 1 to 3 nitrogen, boron, silicon, phosphorus, selenium,oxygen or sulfur atoms, preferably a C₁₋₂₀ alkyl group, a C₆₋₁₀ arylgroup or a C₇₋₂₀ alkylaryl group, or a halogen atom, an OSiR₃ group, aSiR₃ group, a NR₂ group or a PR₂ group (each R represents a C₁₋₁₀hydrocarbon group), but is preferably hydrogen.

When both A and B are an unsubstituted or substituted benzoindenylgroup, or an unsubstituted or substituted indenyl group, they may be thesame or different.

For the production of a copolymer to be used in the present invention,it is particularly preferred that at least one of A and B is anunsubstituted or substituted benzoindenyl group.

Further, it is most preferred that both are an unsubstituted orsubstituted benzoindenyl group.

In the above general formula (1), Y is a methylene group, a silylenegroup, an ethylene group, a germilene group or a boron residue, whichhas bonds to A and B and which further has hydrogen or a groupcontaining a C₁₋₂₀ hydrocarbon (this group may have from 1 to 5nitrogen, boron, silicon, phosphorus, selenium, oxygen, fluorine,chlorine or sulfur atoms), as a substituent. The substituents may be thesame or different from one another. Further, Y may have a cyclicstructure such as a cyclohexylidene group or a cyclopentylidene group.

Preferably, Y is a substituted methylene group or a substituted borongroup, which has bonds to A and B and which is substituted by hydrogen,a C₁₋₂₀ hydrocarbon group, an amino group or a trimethylsilyl group.More preferably, Y is a substituted methylene group, which has bonds toA and B and which is substituted by hydrogen or a C₁₋₂₀ hydrocarbongroup.

The hydrocarbon group may, for example, be an alkyl group, an arylgroup, a cycloalkyl group or a cycloaryl group. The substituents may bethe same or different from one another.

As preferred examples, Y is, for example, —CH₂—, —CMe₂—, —CEt₂—, —CPh₂—,a cyclohexylidene group or a cyclopentylidene group. Here, Me representsa methyl group, Et an ethyl group, and Ph a phenyl group.

Each X is independently hydrogen, a halogen, a C₁₋₁₅ alkyl group, aC₆₋₁₀ aryl group, a C₈₋₁₀ alkylaryl group, a silyl group having a C₁₋₄hydrocarbon substituent, a C₁₋₁₀ alkoxy group, or an amide group or anamino group, which has hydrogen or a C₁₋₂₂ hydrocarbon substituent, andn is an integer of 0, 1 or 2.

The halogen may be chlorine, bromine or fluorine, the alkyl group may,for example, be a methyl group or an ethyl group, the aryl group may,for example, be a phenyl group, the alkylaryl group may, for example, bea benzyl group, the silyl group may, for example, be a trimethylsilylgroup, the alkoxy group may, for example, be a methoxy group, an ethoxygroup or an isopropoxy group, and the amide group may, for example, be adialkylamide group such as a dimethylamide group, or an aryl amide groupsuch as N-methyl anilide, N-phenyl anilide or an anilide group. Further,as X, the groups disclosed in U.S. Pat. Nos. 5,859,276 and 5,892,075 maybe employed.

M is zirconium, hafnium or titanium, particularly preferably zirconium.

As examples of such a transition metal compound, the transition metalcompounds disclosed in EP-0872492A2, JP-A-11-130808, JP-A-9-309925,WO00/20426, EP-0985689A2 and JP-A-6-184179, may be mentioned.

Particularly preferred are transition metal compounds having asubstituted methylene-bridged structure, as specifically disclosed inEP-0872492A2, JP-A-11-130808 and JP-A-9-309925.

As the cocatalyst to be used in the process of the present invention, aknown cocatalyst used in combination is with a conventional transitionmetal compound, or an alkyl aluminum compound may be used. As such acocatalyst, methyl aluminoxane (or may be referred to as methylalumoxane or MAO) or a boron compound is suitably employed. As examplesof the cocatalyst (methyl aluminoxane or a boron compound) or the alkylaluminum compound to be used, the cocatalysts (methyl aluminoxane orboron compounds) or the alkyl aluminum compounds disclosed inEP-0872492A2, JP-A-11-130808, JP-A-9-309925, WO00/20426, EP-0985689A2 orJP-A-6-184179, may be mentioned.

Further, the cocatalyst to be used at that time, is preferably analuminoxane (or may be referred to as an alumoxane) represented by thefollowing general formula (2) or (3).

wherein R is a C₁₋₅ alkyl group, a C₆₋₁₀ aryl group or hydrogen, and mis an integer of from 2 to 100. The plurality of R may be the same ordifferent from one another.

wherein R′ is a C₁₋₅ alkyl group, a C₆₋₁₀ aryl group or hydrogen, and nis an integer of from 2 to 100. The plurality of R′ may be the same ordifferent from one another.

At the time of producing an olefin/aromatic vinyl compound/dienecopolymer to be used in the present invention, the above describedvarious monomers, the transition metal compound (the metal complex) andthe cocatalyst are brought in contact with one another. With respect tothe order of contact and the contacting method, optional known methodsmay be employed.

The above copolymerization or polymerization method may, for example, bea method of polymerizing in a liquid monomer without using a solvent, ora method of employing a single solvent or a mixed solvent selected froma saturated aliphatic or aromatic hydrocarbon or a halogenatedhydrocarbon, such as pentane, hexane, heptane, cyclohexane, benzene,toluene, ethylbenzene, xylene, chloro-substituted benzene,chloro-substituted toluene, methylene chloride or chloroform.Preferably, a mixed alkane type solvent, cyclohexane, toluene orethylbenzene is employed. The polymerization mode may be solutionpolymerization or slurry polymerization. Further, as the case requires,a known method such as batch polymerization, continuous polymerization,preliminary polymerization or multi step polymerization, may beemployed.

Linear or loop, single or connected plural pipe polymerizers may also beemployed. In such a case, the pipe polymerizers may have various knownmixers such as dynamic or static mixers or static mixers equipped with acooling means, or various known coolers such as coolers equipped withcooling slender pipes. Further, they may have a batch type preliminarypolymerizer. Further, a method such as gas phase polymerization may beemployed.

The temperature for polymerization is suitably from −78° C. to 200° C. Apolymerization temperature lower than −78° C., is industriallydisadvantageous, and if it exceeds 200° C., decomposition of thetransition metal compound tends to take place, such being undesirable.

Industrially more preferably, it is from 0° C. to 160° C., particularlypreferably from 30° C. to 160° C.

The pressure during the polymerization is usually from 0.1 atm to 1000atm, preferably from 1 to 100 atm, particularly industrially preferablyfrom 1 to 30 atm.

When alumoxane (or aluminoxane) is used as a cocatalyst, it is used in aratio to the metal of the transition metal compound of from 0.1 to100,000, preferably from 10 to 10,000, by a ratio of aluminum atom/metalatom of the transition metal compound. If the ratio is smaller than 0.1,the transition metal compound cannot effectively be activated, and if itexceeds 100,000, such being economically disadvantageous.

When a boron compound is used as a cocatalyst, it is used in a ratio offrom 0.01 to 100, preferably from 0.1 to 10, particularly preferably 1,by a ratio of boron atom/metal atom of the transition metal compound.

If the ratio is smaller than 0.01, the transition metal compound cannoteffectively be activated, and if it exceeds 100, such being economicallydisadvantageous.

The transition metal compound and the cocatalyst may be mixed andprepared outside the polymerization tank, or may be mixed in the tank atthe time of polymerization.

In the first polymerization step of the present invention, the olefinpartial pressure may be continuously or stepwisely changed within arange of more than 50% and less than 150%, relative to the olefinpartial pressure at the initiation of the polymerization. The olefinpartial pressure in the first polymerization step is preferablymaintained to be constant during the polymerization.

Further, in the first polymerization step of the present invention, theconcentration of the aromatic vinyl compound in the polymerizationsolution can be continuously or stepwisely changed within a range ofmore than 30% and less than 200%, relative to the concentration at theinitiation of the polymerization. Further, it is preferred to set theconversion of the aromatic vinyl compound monomer at a level of lessthan 70% (to set the aromatic vinyl compound concentration higher bymore than 30% as compared with the initiation of the polymerization)without carrying out divided addition of the aromatic vinyl compoundmonomer.

Olefin/aromatic Vinyl Compound/diene Copolymer to be Used in the PresentInvention

The olefin/aromatic vinyl compound/diene copolymer to be used in thepresent invention can be synthesized from the respective monomers of anaromatic vinyl compound, an olefin and a diene by means of a single sitecoordination polymerization catalyst in the above-described firstpolymerization step.

As the olefin/aromatic vinyl compound/diene copolymer obtained in thefirst polymerization step (the main chain polymerization step) of thepresent invention, preferred is an ethylene/styrene/diene copolymer, anethylene,/styrene/α-olefin/diene copolymer or an ethylene/styrene/cyclicolefin/diene copolymer, and particularly preferably, anethylene/styrene/diene copolymer, may be employed.

Further, the olefin/aromatic vinyl compound/diene copolymer obtained inthe first polymerization step (the main chain polymerization step) ofthe present invention may have a cross structure or a crosslinkedstructure with the contained diene monomer units, but it is necessarythat the gel content is less than 10 weight %, preferably less than 0.1weight %, of the entirety.

Now, a typical suitable ethylene/styrene/diene copolymer to be used inthe present invention, will be described.

The ethylene/styrene/diene copolymer obtained by the firstpolymerization step (the main chain polymerization step) preferably hasa chain structure of head-to-tail styrene units attributable to peaksobserved at from 40 to 45 ppm by the 13C-NMR measurement based on TMS.Further, it is preferred to have a chain structure of styrene unitsattributable to peaks observed at 42.3 to 43.1 ppm, 43.7 to 44.5 ppm,40.4 to 41.0 ppm and 43.0 to 43.6 ppm.

Further, the copolymer to be suitably used in the present invention, isan ethylene/styrene/diene copolymer obtainable by means of a metallocenecatalyst capable of producing an isotactic polystyrene byhomopolymerization of styrene, and an ethylene/styrene/diene copolymerobtainable by means of a metallocene catalyst capable of producingpolyethylene by homopolymerization of ethylene.

Therefore, the obtained ethylene/styrene/diene copolymer may haveethylene chain structures, head-to-tail styrene chain structures andstructures having ethylene units and styrene units bonded, in its mainchain.

On the other hand, with conventional so-called pseudo-random copolymers,no styrene head-to-tail chain structure is observed even when thestyrene content is in the vicinity of the maximum of 50 mol %. Further,even if homopolymerization of styrene is attempted by means of acatalyst for the preparation of a pseudo-random copolymer, no polymercan be obtained. Depending upon the polymerization conditions, etc., avery small amount of atactic styrene homopolymer may sometimes beobtainable, but this should be understood to have been formed by cationpolymerization or radical polymerization due to methylalumoxane which iscoexists or due to an alkylaluminum included therein.

The ethylene/styrene/diene copolymer obtainable in the firstpolymerization step (the main chain polymerization step) to bepreferably employed in the present invention, is a copolymer wherein thestereoregularity of phenyl groups in the alternating structure ofstyrene and ethylene represented by the following general formula (4)contained in its structure, is such that the isotactic diad index (orthe meso diad index) m is larger than 0.5, preferably larger than 0.75,particularly preferably larger than 0.95.

The isotactic diad index m of the alternating copolymer structure ofethylene and styrene, can be obtained by the following formula (ii) froman area Ar of the peak attributable to the r structure of the methylenecarbon peak and an area Am of the peak attributable to the m structureappearing in the vicinity of 25 ppm:m=Am/(Ar+Am)  Formula (ii)

The positions of the peaks may sometimes shift more or less dependingupon the measuring conditions or the solvent. For example, whenchloroform-d is used as a solvent, and TMS is used as standard, the peakattributable to the r structure appears in the vicinity of from 25.4 to25.5 ppm, and the peak attributable to the m structure appears in thevicinity of from 25.2 to 25.3 ppm.

Further, when tetrachloroethane-d2 is used as a solvent, and the centerpeak at 73.89 ppm of the triplet of tetrachloroethane-d2 is used asstandard, the peak attributable to the r structure appears in thevicinity of from 25.3 to 25.4 ppm, and the peak attributable to the mstructure appears in the vicinity of from 25.1 to 25.2 ppm.

Here, the m structure represents a meso diad structure, and the rstructure represents a racemic diad structure.

The ethylene/styrene/diene copolymer to be obtained in the firstpolymerization step (the main chain polymerization step) is preferably acopolymer wherein the alternating structure index λ (represented by thefollowing formula (i)) indicating the proportion of the alternatingstructure of styrene and ethylene represented by the general formula (4)contained in the copolymer structure, is smaller than 70 and larger than0.01, preferably smaller than 30 and larger than 0.1.λ=A3/A2×100  Formula (i)wherein A3 is the sum of areas of three peaks a, b and c attributable toan ethylene/styrene alternating structure represented by the followinggeneral formula (4′), obtained by the 13C-NMR measurement, and A2 is thesum of areas of peaks attributable to the main chain methylene andmethane carbon, as observed within a range of from 0 to 50 ppm by13C-NMR using TMS as standard.

(wherein Ph represents a phenyl group and x represents the number ofrepeating units and is an integer of at least 2.)

For at ethylene/styrene/diene copolymer having a diene content of atmost 3 mol %, preferably less than 1 mol %, it is effective to havehead-to-tail styrene chains and/or to have isotactic stereoregularity inthe ethylene/styrene alternating structure, and/or to have analternating structure index λ of smaller than 70, so that it will be anelastomer copolymer having a high transparency and high mechanicalstrength such as breaking strength. A copolymer having suchcharacteristics can be suitably employed in the present invention.

Especially, a copolymer having a high level of isotacticstereoregularity in the ethylene/styrene alternating structure and analternating structure index λ of smaller than 70, is preferred as thecopolymer of the present invention. Further, a copolymer having ahead-to-tail styrene chain, an isotactic stereoregularity in theethylene/styrene alternating structure, and an alternating structureindex λ of smaller than 70, is particularly preferred as the copolymerof the present invention.

Namely, a preferred ethylene/styrene/diene copolymer of the presentinvention has a characteristic such that it has an alternating structureof ethylene and styrene having high stereoregularity and at the sametime has various structures such as ethylene chains having variouslengths, inversion bonds of styrene and styrene chains having variouslengths simultaneously. Further, the ethylene/styrene/diene copolymer ofthe present invention has a characteristic such that the proportion ofthe alternating structure can be variously changeable by the content ofstyrene in the copolymer, the polymerization catalyst or thepolymerization conditions employed, within such a range that the value λobtained by the above formula is more than 0.01 and less than 70.

It is important that the alternating index λ is lower than 70 in orderto present significant mechanical strength, solvent resistance,toughness and transparency despite a crystallizable polymer, or in orderto be a partially crystallizable polymer, or in order to be anon-crystallizable polymer.

The above-described olefin/aromatic vinyl compound/diene copolymer to bepreferably employed in the present invention, particularly anethylene/styrene/divinylbenzene copolymer, can be obtained by means of apolymerization catalyst comprising a transition metal compoundrepresented by the above general formula (1) and a cocatalyst.

In the foregoing, as a typical preferred example of the olefin/aromaticvinyl compound/diene copolymer to be used in the present invention, anethylene/styrene/diene copolymer has been described, but theolefin/aromatic vinyl compound/diene copolymer to be used in the presentinvention is not, of course, limited to this.

The weight average molecular weight of the olefin/aromatic vinylcompound/diene copolymer to be used in the present invention is at least10,000, preferably at least 30,000, particularly preferably at least60,000, and at moist 1,000,000 preferably at most 500,000. The molecularweight distribution (Mw/Mn) is not particularly limited, but is usuallyat most 6, preferably at most 4, most preferably at most 3.

Here, the weight average molecular weight is a molecular weightcalculated as polystyrene obtained by using standard polystyrene by GPC.The same will apply to the following description.

The weight average molecular weight of the olefin/aromatic vinylcompound/diene copolymer to be used in the present invention can beadjusted as the case requires, within the above range, by a known methodemploying a chain transfer agent such as hydrogen or by changing thepolymerization temperature.

The olefin/aromatic vinyl compound/diene copolymer obtainable in thefirst polymerization step (the main chain polymerizations step) of thepresent invention may have a partially crossing structure or branchedstructure via diene units contained.

Further, another embodiment of the present invention is anolefin/aromatic vinyl compound/divinylbenzene copolymer having anaromatic vinyl compound content of from 0 mol % to 96 mol %, preferablyfrom 0.03 mol % to 96 mol %, a diene content of from 0.0001 mol % to 3mol %, the rest being an olefin, obtained by copolymerizingm-divinylbenzene having an isomer purity of at least 80 weight %,preferably at least 90 weight %, an olefin and an aromatic vinylcompound. Such an olefin/aromatic vinyl compound/divinylbenzenecopolymer can be obtained by the process disclosed in the presentinvention, and it is useful preferably for the production of thecross-copolymerized olefin/aromatic vinyl compound/diene copolymer ofthe present invention. Further, it may be used for other applications,such as for the production of a cross-linked polymer, by e.g. a radicalmethod or electron ray cross linking, or as a resin additive or amodifying material.

B) Second Polymerization Step (crossing step)

As the second polymerization step of the present invention, coordinationpolymerization employing the above-mentioned single site coordinationpolymerization catalyst, is employed. Preferably, a single sitecoordination polymerization catalyst comprising a transition metalcompound represented by the same general formula (1) as in the firstpolymerization step and a cocatalyst, is employed. This single sitecoordination polymerization catalyst comprising a transition metalcompound represented by the general formula (1) and a cocatalyst, iscapable of copolymerizing residual coordination polymerizable doublebonds of diene units, particularly divinylbenzene, copolymerized to thepolymer main chain, at high efficiency, and it is preferred in thepresent invention. In the second polymerization step of the presentinvention, it is most preferred, to employ the same single sitecoordination polymerization catalyst as used in the first polymerizationstep, (the same transition metal compound, and the same cocatalyst). Thecopolymer obtainable in the second polymerization step of the presentinvention preferably has the same structure as the copolymer in theabove-mentioned first polymerization step.

In the second polymerization step of the present invention, the samemethod as the polymerization method employed, in the above-mentionedfirst polymerization step, is employed. In this case, the respectivemonomers employed in the above-mentioned first polymerization step, theolefin, the aromatic vinyl compound, and, if necessary, the dieneremaining in the polymerization solution, may be employed.

The second polymerization of the present invention is preferably carriedout following the first polymerization step by using the polymerizationsolution obtained in the above first polymerization step. However, thesecond polymerization step may be carried out in the presence of asingle site coordination polymerization catalyst by recovering thecopolymer obtained in the above first polymerization step from thepolymerization solution, dissolving it in a new solvent and addingmonomers to be employed.

The aromatic vinyl compound content is required to be different by atleast 5 mol %, preferably 10 mol %, most preferably at least 15 mol %,as between the olefin/aromatic vinyl compound/diene copolymer to bepolymerized in the first polymerization step (the main chainpolymerization step), of the present invention and the olefin/aromaticvinyl compound copolymer or the olefin/aromatic vinyl compound/dienecopolymer to be polymerized in the second or subsequent polymerizationstep (the crossing step) (when the polymerization solution obtained inthe first polymerization step is used as it is, in the second orsubsequent polymerization step, the resulting polymer will have a smallamount of a residual diene copolymerized). In an extreme case, thearomatic vinyl compound content in the olefin/aromatic vinyl compoundcopolymer to be polymerized in the second or subsequent polymerizationstep (the crossing step) may be 0 mol %. In this case, it is preferredto carry out the second polymerization step by recovering the copolymerfrom the polymerization solution obtained in the first polymerizationstep and dissolving it in a new solvent, and adding a catalyst, acocatalyst and an olefin.

Further, the aromatic vinyl compound content in the olefin/aromaticvinyl compound/(diene copolymer obtainable in the first polymerizationstep and the aromatic vinyl compound content in the finally obtainablecross-copolymerized olefin/aromatic vinyl compound/diene copolymer, arerequired to be different by at least 2 mol %, preferably at least 5 mol%, more preferably at least 10 mol %.

The polymer obtainable in the second polymerization step (the crosschain polymerization step) of the present invention may have a partiallycrossing structure or a branched structure via diene units contained.

In a case where the polymerization solution obtained in the firstpolymerization step is employed in the second polymerization step, anunreacted diene remaining in the polymerization solution will becopolymerized in the second polymerization step, and the diene contentis usually within a range of from 0.0001 mol % to 3 mol %, preferablyfrom 0.001 mol % to less than 0.5 mol %, in the olefin/aromatic vinylcompound copolymer (inclusive of cross chains) to be obtained in thesecond polymerization step. If the diene content is higher than thisrange, the finally obtainable cross copolymer tends to be insolubilizedor gelled to deteriorate the processability, such being undesirable.

A specific process for producing the cross-copolymer of the presentinvention, which satisfies the foregoing, will be described below.

Namely, it is a process for producing a cross-copolymerizedolefin/aromatic vinyl compound/diene copolymer, employing apolymerization method of at least two steps comprising as the firstpolymerization step (the main chain polymerization step) carrying outcopolymerization of an aromatic vinyl compound monomer, an olefinmonomer and a diene monomer by means of a coordination polymerizationcatalysts to synthesize an olefin/aromatic vinyl compound/dienecopolymer, and then as the second polymerization step (the crossingstep) under polymerization conditions different therefrom, carrying outpolymerization by means of a coordination polymerization catalyst in theco-existence of this olefin/aromatic vinyl compound/diene copolymer andat least an olefin and an aromatic vinyl compound monomer. Further,preferred is a process satisfying at least one of the followingconditions.

1) The olefin partial pressure of the polymerization system in thesecond or subsequent polymerization step is at least 150% or at most50%, relative to the olefin partial pressure at the initiation of thefirst polymerization step. However, industrially, the olefin partialpressure in the second or subsequent polymerization step is at most 1000atm, preferably at most 100 atm.

On the other hand, in the present invention, the olefin partial pressurein the first, polymerization step is adjusted within a range of higherthan 50% and lower than 150% of the olefin pressure at the initiation ofthe polymerization, but the olefin partial pressure is more preferablyconstant.

2) The concentration of the aromatic vinyl compound in thepolymerization solution at the initiation of the second or subsequentpolymerization step is at most 30% or at least 200%, relative to theconcentration of the aromatic vinyl compound at the initiation of thefirst polymerization step.

However, the concentration of the aromatic vinyl compound in the firststep in the present invention, is maintained within a range higher than30% of the concentration at, the initiation of the polymerization.

3) In the first polymerization step and the second or subsequentpolymerization step, different single site coordination polymerizationcatalysts are employed.

4) In the first polymerization step and the second or subsequentpolymerization step, the type of the olefin to be used forpolymerization is different.

The first polymerization step and the second polymerization step aredistinguished at such a time point that an operation for such change ofconditions has been initiated, or at such a time point that such changeof conditions has been satisfied.

The change to satisfy the above conditions is preferably carried out andcompleted as quickly as possible, preferably within 50%, more preferablywithin 30%, most preferably within 10% of the polymerization time in thesecond polymerization step.

The polymerization temperatures in the first polymerization step and thesecond polymerization step are preferably the same. If they aredifferent, the temperature difference is suitably within about 100° C.

As a method for changing the compositional ratio of monomers in thepolymerization solution, a method is available wherein the olefinpartial pressure of the polymerization system in the second orsubsequent polymerization step is changed at least 150%, preferably200%, most preferably at least 300%, relative to the firstpolymerization step. For example, in a case where ethylene is employedas the olefin, when the first polymerization step is carried out underan ethylene pressure of 0.2 MPa, the second polymerization step iscarried out under a pressure of at least 0.3 MPa, preferably at least0.4 MPa, most preferably at least 0.6 MPa.

Further, the olefin partial pressure of the polymerization system in thesecond or subsequent polymerization step may be changed to at most 50%,preferably at most 20%, relative to the first polymerization step. Forexample, when the first polymerization step is carried out under anethylene pressure of 1.0 MPa, the second polymerization step is carriedout under a pressure of almost 0.5 MPa, preferably at most 0.2 MPa.

The olefin pressure in the second polymerization step may be constant orchanged stepwisely or continuously during the polymerization so long asit satisfies the above conditions.

Further, as a method for changing the compositional ratio of monomers inthe polymerization solution, a method may be employed wherein theconcentration of the aromatic vinyl compound in the polymerizationsolution at the initiation of the polymerization in the second orsubsequent polymerization step, is changed to at most 30%, preferably atmost 20%, or at least 200%, preferably at least 500%, relative to thefirst polymerization step. For example, in a case where styrene isemployed as the aromatic vinyl compound, when the first polymerizationstep is initiated at a styrene concentration in the polymerizationsolution of 1 mol %/l, the second polymerization step is carried out ata concentration of at most 0.5 mol/l, preferably at most 0.2 mol/l, orat least 2 mol/l, preferably at least 5 mol/l. Further, changes of theabove olefin partial pressure and the concentration of the aromaticvinyl compound may be applied in combination.

When the second polymerization step is carried out in the presence of asingle site coordination polymerization catalyst by recovering thecopolymer obtained in the first polymerization step from thepolymerization solution and dissolving it in a new solvent, and addingan olefin and an aromatic vinyl compound monomer, it is possible toemploy a single site polymerization catalyst which is different from thefirst polymerization step.

By changing the type of the olefin to be used for the polymerization inthe first polymerization step and the second or subsequentpolymerization step, the content of the aromatic vinyl compound in thecopolymer polymerized in the first polymerization step, and the secondpolymerization step or the content of the aromatic vinyl compound in thecross-copolymer finally obtainable, can be changed as described above.

In a case where the second polymerization step is carried outcontinuously after the first polymerization step employing thepolymerization solution obtained in the above first polymerization step,and the monomers remaining in the polymerization solution of the firstpolymerization step are used for the second polymerization step withoutaddition of a new aromatic vinyl compound monomer, the conversion of thearomatic vinyl compound monomer species throughout the entirepolymerization steps is preferably at least 50 weight %, particularlypreferably at least 60 weight %. As the conversion of the aromatic vinylcompound monomer becomes higher, the probability that the polymerizabledouble bonds of diene units in the main chain of the copolymer arecross-copolymerized, will increase.

For the production of the cross-copolymer of the present invention, itis preferred to employ a process which satisfies 1) and 2) among theabove conditions.

Namely, in the second polymerization step, it is preferred to employ thesame, single site coordination polymerization catalyst (the sametransition metal compound and the same cocatalyst) as in the firstpolymerization step.

Further, it is preferred that in the first polymerization step and thesecond or subsequent polymerization step, the type of the olefin to beused for polymerization is the same.

Further, for the production of the cross-copolymer of the presentinvention, it is most preferred to employ a process which satisfies 1)among the above conditions.

For the production of the cross-copolymer of the present invention, mostpreferably, a method is employed wherein the olefin partial pressure ofthe polymerization system in the second or subsequent polymerizationstep is changed at least 300%, relative to the first polymerizationstep.

Further, in a case where the olefin partial pressure in the secondpolymerization step is not constant, i.e. in a case where it varieswithin the above range, most preferably, a method is employed whereinthe olefin partial pressure in the second or subsequent polymerizationstep is changed at least 300%, relative to the olefin partial pressureat the initiation of the first polymerization step.

The proportion of the copolymer obtained in the first polymerizationstep is required to be at least 10 weight %, preferably at least 30weight % of the cross-copolymer finally obtainable. Further, the amountof the polymer (inclusive of the weight of cross chains) obtainable inthe second polymerization step is required to be at least 10 weight %,preferably at least 30 weight % of the cross-copolymer finallyobtainable. If the proportion of the copolymer obtained in the firstpolymerization step or in the second polymerization step is less than 10weight % of the finally obtainable cross-copolymer, the characteristicsof the copolymer of the small amount component can not adequately beobtained.

The first polymerization step and the second polymerization step may becarried out in separate reactors. These steps may be carried out bymeans of a single reactor. In such a case, these steps are distinguishedat such a time point that the operation for the change of the conditionsas described in the above 1) to 4) has been initiated, or at such a timepoint that the change of such conditions has been satisfied.

The cross-copolymer of the present invention may be produced in a singlereactor by carrying out copolymerization of an olefin, an aromatic vinylcompound and a diene by means of a coordination polymerization catalystwhile changing the olefin or aromatic vinyl compound, concentrationcontinuously. It will suffice that at least the of the condition changesof the above 1) to 4) is satisfied substantially at the initiation andcompletion of the polymerization.

Further, the cross-copolymer of the present invention is across-copolymer excellent in the mold processability, characterized inthat MFR (melt flow rate) as measured under a load of 5 kg at 230° C. isat least 1.0 g/10 min and at most 50 g/10 min. A process for producingsuch a cross-copolymer of the present invention is not particularlylimited, but a process which satisfies at least one of the followingproduction conditions, is preferred.

a) In the first and/or second polymerization step, the polymerizationtemperature is substantially always at least 80° C., preferably at least85° C. and at most 160° C.

b) The aromatic vinyl compound content of the polymer obtained in thefirst polymerization step, is at least 30 mol %, and its weight averagemolecular weight is at most 250,000.

c) The diene to be employed, is m-divinylbenzene having an isomer purityof at least 80 weight %, preferably at least 90 weight %.

The cross-copolymer of the present invention can be produced by aprocess comprising the above-mentioned first polymerization step (themain chain polymerization step) and the second polymerization step (thecrossing step). For this process, a conventional optional method may beemployed. For example, a method may be employed wherein the firstpolymerization step is carried out by completely mixed type batchpolymerization or continuous polymerization, and the secondpolymerization step is carried out also by similar batch polymerizationor continuous polymerization, or a method may be employed wherein thefirst polymerization step is carried out by completely mixed type batchpolymerization or continuous polymerization, and the secondpolymerization step is carried out by plug flow polymerization. Here,completely mixed type polymerization is a conventional method wherein,for example, a tank-form, a tower form or loop-form reactor is employed,and it is a polymerization method wherein in the reactor, thepolymerization solution is stirred and mixed relatively well to have asubstantially uniform composition. Further, plug flow polymerization isa polymerization method wherein in the reactor, mass transfer isrestricted, and the polymerization solution has a continuous ornon-continuous compositional distribution from the inlet towards theoutlet of the reactor. In the second polymerization step of the presentinvention, a polymerization means of a loop type or a plug flow typehaving a pipe-form equipped with various cooling and mixing means ispreferred with a view to carrying out heat removal efficiently, sincethe viscosity of the polymerization solution increases.

Now, the physical properties of a cross-polymerizedethylene/styrene/divinylbenzene copolymer as a typical example of thecross-copolymerized olefin/aromatic vinyl compound/diene copolymer ofthe present invention, and the applications thereof will be described.

The cross-copolymer of the present invention is characterized in thatthe compositions (the styrene contents) of the main chain and the crosschain are substantially different. Either the main chain or the crosschain may have a composition having a low styrene content (i.e. acrystal structure derived from ethylene chains). Further, thecross-copolymer of the present invention may contain ethylene/styrenecopolymers (which may contain a small amount of divinylbenzene) havingdifferent styrene contents corresponding respectively to the styrenecontents of the main chain and the cross chain in an optional ratio.However, since the cross-copolymer functions as a compatibilizing agentfor them, it can have various characteristics and high transparency atthe same time.

The cross-copolymer of the present invention has good heat resistance,since it has a crystal structure derived from ethylene chains. Further,it can also have characteristics such as high mechanical properties(breaking strength, tensile modulus) and a low glass transitiontemperature or a low brittle temperature (at most −50° C.) which anethylene/styrene copolymer having a low styrene content has. Further,either the main chain or the cross chain can have a composition having arelatively high styrene content, whereby the product can have thecharacteristics of an ethylene/styrene copolymer having a relativelyhigh styrene content, as described below. Namely, it can have arelatively low tensile modulus, surface hardness, flexibility, a tan δcomponent in the vicinity of room temperature in the is viscoelasticityspectrum (0.05 to 0.80 at 0° C. or 25° C.), an antiscratching property,a feeling like polyvinyl chloride, a painting property and printability.

Further, with the cross-copolymer of the present invention, the hardnesscan optionally be changed within the scope of a soft resin from arelatively hard resin (a shore A hardness of at least 88) to a softresin (a shore A hardness of at most 87 and at least about 60) bychanging the weight ratio of the main chain copolymer (the copolymercomponent obtained in the first polymerization step) and the cross chaincopolymer (the copolymer component obtained in the second polymerizationstep). Particularly, in order to make the shore A hardness of thecross-copolymer of the present invention to be at most 87, it ispreferred that either copolymer obtained in the first polymerizationstep or the second polymerization step is substantially non-crystalline,and this substantially non-crystalline copolymer occupies at least 60weight % in the finally obtainable cross-copolymer. Further, it isparticularly preferred that the copolymer obtained in the firstpolymerization step is substantially non-crystalline, and thissubstantially non-crystalline copolymer occupies at least 60 weight % ofthe finally obtainable cross copolymer. Here, substantiallynon-crystalline means that the melting point of the crystal peakobserved by DSC is at most 70° C., more preferably, its heat of fusionis at most 15 J/g, or the crystallinity (crystallization ratio)calculated by an X-ray diffraction method is at most 10%. Further, forthe shore A hardness of the cross-copolymer of the present invention tobe at most 87 at room temperature, it is important that the glasstransition point of the copolymer obtained in the first polymerizationstep is at most 5° C., preferably at most 0° C.

The cross-copolymerized ethylene/styrene/diene copolymer of the presentinvention may be used alone and can suitably be employed as a substitutefor a known transparent soft resin such as soft polyvinyl chloride.

To the cross-copolymer of the present invention, a stabilizer, anaging-preventing agent, a light resistance-improving agent, anultraviolet absorber, a plasticizer, a softening agent, a lubricant, aprocessing adjuvant, a colorant, an antistatic agent, an anti-foggingagent, a blocking-preventing agent, a crystal nucleating agent, etc.which are commonly used for resins, may be incorporated. These additivesmay be used alone or in combination of a plurality of them.

By virtue of the excellent characteristics, the cross-copolymer of thepresent invention is used alone or as a composition containing it as themain component and can be suitably used for a stretch film, a shrinkfilm, a packaging material, a sheet, a tube or a hose as a substitutefor a known transparent soft resin such as soft polyvinyl chloride.

Application to Films

In a case where the cross-copolymer of the present invention is used asa film or a stretch packaging film, the thickness is not particularlylimited, but it is usually from 3 μm to 1 mm, preferably from 10 μm to0.5 mm. To use it as a stretch packaging film for foods, the thicknessis preferably from 5 to 100 μm, more preferably from 10 to 50 μm.

For the production of a transparent film or a stretch packaging filmmade of the cross-copolymer of the present invention, a common extrusionfilm-forming method such as an inflation system or a T-die system, maybe employed. For the purpose of improving the physical properties, thefilm or the stretch packaging film of the present invention may belaminated with other suitable film, for example, a film of e.g.isotactic or syndiotactic polypropylene, high density polyethylene, lowdensity polyethylene (LDPE or LLDPE), polystyrene, polyethyleneterephthalate or an ethylene/vinyl acetate copolymer (EVA).

Further, the film or the stretch packaging film of the present inventionmay have self-tackiness or an adhesive property by suitably selectingthe composition of the main chain or the cross chain. However, if astronger self-tackiness is required, it may be laminated with other filmhaving self-tackiness to obtain a multi-layered film.

Further, when a stretch packaging film having a non-tacky surface and atacky surface on the front and rear sides, is desired, the non-tackysurface may be made of an ethylene/styrene copolymer having a higherethylene content or a linear low density polyethylene having a densityof at least 0.916 g/cm³ in a thickness of from 5 to 30% of the totalthickness, the interlayer may be made of the ethylene/styrene copolymerto be used in the present invention, and the tacky layer may be made ofone having from 2 to 10 weight % of liquid polyisobutylene, liquidpolybutadiene or the like incorporated to the ethylene/styrene copolymerto be used in the present invention, one having from 2 to 10 weight % ofliquid polyisobutylene, liquid polybutadiene or the like incorporated toa linear low density polyethylene having a density of at least 0.916g/cm³, or an ethylene/vinyl acetate copolymer, in a thickness of from 5to 30% of the total thickness, to obtain a multilayer film. Otherwise,it is also possible to incorporate a suitable tackifier in a suitableamount.

Specific applications of the film of the present invention are notparticularly limited, but it is useful as a general packaging materialor a container and can be used for e.g. a packaging film, a bag or apouch. Especially, it can suitably be used as a stretch packaging filmor a pallet stretching film for food packaging.

To the molded product, particularly the film or the stretch packagingfilm, of the present invention, surface treatment with e.g. corona,ozone or plasma, coating with an anti-fogging agent, coating with alubricant or printing, may be applied, as the case requires.

Among molded products of the present invention, the film or the stretchpackaging film may be prepared as a monoaxially or biaxially stretchedfilm, as the case requires.

The film or the stretch packaging film of the present invention may bebonded to the film itself or to a material such as other thermoplasticresin by fusion by means of e.g. heat, supersonic waves, microwave or bybonding by means of e.g. a solvent.

Further, when used as a stretch packaging film for foods, it can besuitably packaged by an automatic packaging machine or a manualpackaging machine.

Further, when the film of the present invention has a thickness of, forexample, at least 100 μm, a packaging tray for foods, electricalproducts, etc., can be molded by a technique such has heat molding,vacuum molding, compression molding or air-pressure forming.

Further, the cross-copolymer of the present invention basically does notcontain an elutable plasticizer or halogen and thus has a basiccharacteristic that its environmental compatibility or safety is high.

The cross-copolymer of the present invention may be used as acomposition with other polymers.

Known polymers or additives for the conventional compositions with anethylene/styrene copolymer, can also be employed for a composition withthe cross-copolymer of the present invention. The following may bementioned as such polymers and additives. The following polymers may beadded within a range of from 1 to 99 parts by weight, preferably from 30to 95 parts by weight, based on the composition employing thecross-copolymer of the present invention. Further, the cross-copolymerof the present invention can be used also as a compatibilizing agent for“an aromatic vinyl compound type polymer” and “an olefin type polymer”.With the cross-copolymer of the present invention, the olefin/aromaticvinyl compound content ratio in the main chain and the cross chain cansubstantially be changed, whereby it is possible to increase thecompatibility with the respective polymers, and it is suitably employedas a compatibilizing agent for that purpose. In this case, thecross-copolymer of the present invention can be used within a range offrom 1 to 50 parts by weight, preferably from 1 to 20 parts by weight,based on the composition. Further, in the case of “a filler” or “aplasticizer”, it can be used within a range of from 1 to 80 parts byweight, preferably from 5 to 50 parts by weight, based on thecomposition.

Aromatic Vinyl Compound Type Polymer

A homopolymer of an aromatic vinyl compound, and a copolymer of anaromatic vinyl compound with at least one monomer componentcopolymerizable therewith, wherein the aromatic vinyl compound contentis at least 10 weight %, preferably at least 30 weight %. The aromaticvinyl compound monomer to be used for the aromatic vinyl compound typepolymer includes styrene and various substituted styrenes such asp-methylstyrene, m-methylstyrene, o-methylstyrene, o-t-butylstyrene,m-t-butylstyrene, p-t-butylstyrene and α-methylstyrene, and further, acompound having a plurality of vinyl groups in one molecule, such asdivinylbenzene, may also be mentioned. Further, a copolymer of aplurality of such aromatic vinyl compounds, may also be employed. Thestereoregularity among mutual aromatic groups of the aromatic vinylcompound may be atactic, isotactic or syndiotactic.

The monomer copolymerizable with the aromatic vinyl compound includesbutadiene, isoprene, other conjugated dienes, acrylic acid, methacrylicacid and amide derivatives or ester derivatives, maleic anhydride andits derivatives. The copolymerization mode may be any one of blockcopolymerization, tapered block copolymerization, randomcopolymerization and alternating copolymerization. Further, it may beone having the above aromatic vinyl compound graft-polymerized to apolymer made of the above-mentioned monomers, which contains at least 10weight %, preferably at least 30 weight %, of the aromatic vinylcompound.

The above aromatic vinyl compound type polymer is required to have aweight average molecular weight of at least 30,000, preferably at least50,000, as calculated as styrene, in order to show the performance as apractical resin.

The aromatic vinyl compound type resin to be used, may, for example, beisotactic polystyrene (i-PS), syndiotactic polystyrene (s-PS), atacticpolystyrene (a-PS), rubber-reinforced polystyrene (HIPS), anacrylonitrile/butadiene/styrene copolymer (ABS) resin, astyrene/acrylonitrile copolymer (AS resin), a styrene/methacrylatecopolymer such as a styrene/methyl methacrylate copolymer, astyrete/diene block/tapered copolymer (such as SBS, SIS), a hydrogenatedstyrene/diene block/tapered copolymer (such as SEBS, SEPS), astyrene/diene copolymer (such as SBR), a hydrogenated styrene/dienecopolymer (such as hydrogenated SBR), a styrene/maleic acid copolymer,or a styrene/imidated maleic acid copolymer. Further, it is a conceptincluding a petroleum resin.

Olefin Type Polymer

For example, low density polyethylene (LDPE), high density polyethylene(HDPE), linear low density polyethylene (LLDPE), isotactic polypropylene(i-PP), is syndiotactic polypropylene (s-PP), atactic polypropylene(a-PP), a propylene/ethylene block copolymer, a propylene/ethylenerandom copolymer, an ethylene/propylene/diene copolymer (EPDM), anethylene/vinyl acetate copolymer, polyisobutene, polybutene, a cyclicolefin polymer such as polynorbornene and a cyclic olefin copolymer suchas an ethylene/norbornene copolymer, may be mentioned. It may be anolefin type resin co-polymerized with a diene such as butadiene orα-ω-diene, as the case requires.

The above olefin type polymer is required to have a weight averagemolecular weight of at least 10,000, preferably at least 30,000, ascalculated as styrene, in order to show the performance as a practicalresin.

Other Resins, Elastomers and Rubbers

For example, polyamide such as nylon, polyimide, polyester such aspolyethylene terephthalate, polyvinyl alcohol, and a styrene type blockcopolymer such as SBS (styrene/butadiene block copolymer), SEBS(hydrogenated styrene/butadiene block copolymer), SIS (styrene/isopreneblock copolymer), SEPS (hydrogenated styrene/isoprene block copolymer),SBR (styrene/butadiene block copolymer) or hydrogenated SBR, which isnot in the scope of the above aromatic vinyl compound type resin,natural rubber, a silicone resin, and silicone rubber, may be mentioned.

Fillers

Known fillers may be employed. As preferred examples, calcium carbonate,talc, clay, calcium silicate, magnesium carbonate, magnesium hydroxide,mica, barium sulfate, titanium oxide, aluminum hydroxide, silica, carbonblack, wood powder and wood pulp may, for example, be mentioned.Further, glass fibers, known graphites or conductive fillers such ascarbon fibers, may also be employed.

Plasticizers

Known plasticizers, such as paraffin type, naphthene type or aroma typeprocess oils, mineral oil type softening agents such as liquid paraffin,castor oil, linseed oil, olefin type wax, mineral type wax and variousesters, may be used.

For the production of the polymer composition of the present invention,a suitable known blending method may be employed. For example,melt-mixing can be carried out by means of a single screw or twin screwextruder, a Banbury mixer, a plasto mill, a co-kneader or a heated roll.Prior to the melt mixing, it is advisable to uniformly mix therespective materials by means of e.g. a Henschel mixer, a ribbonblender, a super mixer or a tumbler. The melt mixing temperature is notparticularly limited, but it is usually from 100 to 300° C., preferablyfrom 150 to 250° C.

As molding methods for various compositions of the present invention,known molding methods such as vacuum molding injection molding, blowmolding, extrusion molding or profile extrusion molding, may beemployed.

The composition containing the cross-copolymer of the present inventioncan be preferably used as various film or packaging materials, sheets,tubes, hoses, gaskets, and further as building materials such as floormaterials or wall materials, or interior materials for automobiles.

Now, the present invention will be described with reference to Examples,but the present invention is by no means restricted to the followingExamples.

The analyses of copolymers obtained in the respective Examples andComparative Examples were carried out by the following methods.

The 13C-NMR spectrum was measured by using TMS as standard, by using achloroform-d solvent or a 1,1,2,2-tetrachloroethane-d2 solvent, by meansof α-500 manufactured by Nippon Denshi Kabushiki Kaisha. Here, themeasurement using TMS as standard is the following measurement. Firstly,using TMS as standard, the shift value of the center peak of triplet13C-NMR peaks of 1,1,2,2-tetrachloroethane-d2 was determined. Then, thecopolymer was dissolved in 1,1,2,2-tetrachloroethane-d2, and the 13C-NMRwas measured, whereby each peak shift value was calculated, based on thetriplet center peak of 1,1,2,2-tetrachloroethane-d2. The shift value ofthe triplet center peak of 1,1,2,2-tetrachloroethane-d2 was 73.89 ppm.The measurement was carried out by dissolving the polymer in suchsolvent in an amount of 3 weight/volume %.

The 13C-NMR spectrum measurement for quantitive analysis of peak areas,was carried out by a proton gate decoupling method having NOE erased, byusing pulses with a pulse width of 45° and a repeating time of 5 secondsas standard.

When the measurement was carried out under the same conditions exceptthat the repeating time was changed to 1.5 seconds, the measured valuesof peak areas of the copolymer agreed to the values obtained in the casewhere the repeating time was 5 seconds, within measurement error.

The styrene content in the copolymer was determined by 1H-NMR. As theapparatus, α-500 manufactured by Nippon Denshi Kabushiki Kaisha andAC-250 manufactured by BRUCKER COMPANY, were employed. The determinationwas carried out at a temperature of from 80 to 100° C. by dissolving asample in 1,1,2,2-tetrachloroethane-d2 and comparing the intensity ofthe proton peak attributable to a phenyl group (6.5 to 7.5 ppm) and theproton peak attributable to an alkyl group (0.8 to 3 ppm), measured byusing TMS as standard.

The diene (divinylbenzene) content was measured by 1H-NMR.

As the molecular weights in Examples, weight average molecular weightsas calculated as standard polystyrene, were obtained by means of GPC(Gel Permeation Chromatography).

A copolymer soluble in THF at room temperature, was measured by means ofHLC-8020manufactured-by TOSOH CORPORATION using THF as the solvent.

A copolymer insoluble in THF at room temperature, was measured either at135° C. by means of 150CV apparatus manufactured by Waters Company using1,2,4-trichlorobenzene as the solvent or at 145° C. by means of HLC-8121apparatus manufactured by TOSOH CORPORATION using o-chlorobenzene as thesolvent. As the detector, RI (differential refractive index meter) wasused. With cross-copolymers in Examples, the refractive index too-dichlorobenzene as the solvent is reversed between the main chaincomponent and the cross chain component. Accordingly, the molecularweight of a cross-copolymer obtained by the RI detector is not accurateand is useful only as a reference value.

The DSC measurement was carried out by using DSC 200 manufactured bySeiko Denshi K.K. in a nitrogen stream at a temperature raising rate of10° C./min. Using 10 mg of a sample, it was heated to 240° C. at atemperature raising rate of 20° C./min and quenched to −100° C. or lowerby liquid nitrogen (pretreatment), and then the temperature was raisedfrom −100° C. at a rate of 10° C./min to carry out the DSC measurementup to 240° C., whereby the melting point, the heat of crystal fusion andthe glass transition point were obtained. The glass transition point wasobtained by a tangent method.

As a sample for evaluation of the physical properties, a sheet havingthickness of 1.0 mm formed by a heat-pressing method (temperature: 180°C., time: 3 minutes, pressure: 50 kg/cm²) was used.

Tensile Test

In accordance with JIS K-6251, the sheet was cut into a shape of testpiece No. 1, and measured at a tensile speed of 500 mm/min by means ofAGS-100D model tensile tester manufactured by Shimadzu Corporation.

Permanent Elongation

The strain recovery in a tensile test was measured by the followingmethod.

Using the JIS No. 2 small size (½) test piece, it was pulled by atensile tester to a strain of 100% and maintained for 10 minutes, whereupon the stress was quickly released (without repulsion) and the strainrecovery after 10 minutes was represented by %.

Vicat Softening Point

A sheet having a thickness of 4 mm was prepared by a heat pressingmethod, and a test specimen of 10 mm×10 mm was cut out. In accordancewith JIS K-7206, it was measured under a load of 320 g at an initialtemperature of 40° C. under a temperature raising condition of 50° C./hrusing HDT & VSPT tester S3-FH, manufactured by Toyo Seiki.

Measurement of Dynamic Viscoelasticity

Using a dynamic viscoelasticity measuring apparatus (RSA-II,manufactured by Rheometrix Company), the loss tan δ was measured at afrequency of 1 Hz within a temperature range of from −120° C. to +150°C. (the measuring temperature range was slightly changed depending uponthe properties of the sample). From a sheet having a thickness of 0.1 mmprepared by heat pressing, a sample for measurement (3 mm×40 mm) wasobtained.

X-ray Diffraction

The X-ray diffraction was measured by MXP-18 model high power X-raydiffraction apparatus, manufactured by Mac Science Company employing asthe ray source a Cu sealed counter cathode (wavelength: 1.5405 Å).

Hardness

With respect to the hardness, durometer hardness of types A and D wasobtained in accordance with the test method for durometer hardness ofplastics as prescribed in JIS K-7215. This hardness is an instantaneousvalue.

Total Light Transmittance, Haze

With respect to the transparency, the total light transmittance and thehaze were measured by means of turbidity meter NDH2000, manufactured byNippon Denshoku Kogyo K. K. in accordance with the test method foroptical characteristics of plastics as prescribed in JIS K-7105 withrespect to a sheet having a thickness of 1 mm molded by heat pressing(temperature: 200° C., time: 4 minutes, pressure: 50 kg/cm²G).

Divinylbenzene

The divinylbenzene (a mixed product of m-isomer and p-isomer) used inthe following Examples 1 to 3 relating to the cross-copolymer wasmanufactured by Aldrich Company (purity as divinylbenzene: 80%, amixture of m-isomer and p-isomer, weight ratio ofmeta-form:para-form=70:30, accordingly, the isomer purity ofm-divinylbenzene is 70 weight %). In the following polymerization, when1 ml (5.5 mmol as divinylbenzene) was used per 400 ml of styrene, theamount of divinylbenzene corresponds to 1/640 of the amount of styreneby molar ratio.

Catalyst (transition metal compound)

In the following Examples, as a transition metal compound (catalyst),rac-dimethylmethylenebis (4,5-benzo-1-indenyl)zirconium dichloride,(rac-isopropylidenebis(4,5-benzo-1-indenyl)zirconium dichloride) wasemployed.

rac-dimethylmethylenebis(4,5-benzo-1-indenyl)zirconium dichloride

EXAMPLE 1 Preparation of a Cross-copolymerizedEthylene/styrene/divinylbenzene Copolymer

Using rac-dimethylmethylenebis(4,5-benzo-1-indenyl)zirconium dichlorideas a catalyst, the preparation was carried out as follows.

Polymerization was carried out by means of an autoclave having acapacity of 10 l and equipped with a stirrer and a jacket for heatingand cooling.

4400 ml of toluene, 400 ml of styrene and 1.0 ml of divinylbenzenemanufactured by Aldrich Company were charged and heated and stirred atan internal temperature of 70° C. About 200 l of nitrogen was bubbled topurge the interior of the system and the polymerization solution. 8.4mmol of triisobutyl aluminum and 21 mmol, based on Al, of methylalumoxane (PMAO-3A, manufactured by TOSOH AKZO K. K.) were added, andethylene was immediately introduced. After the pressure was stabilizedat 0.25 MPa (1.5 kg/cm²G), from a catalyst tank installed above theautoclave, about 50 ml of a toluene solution having 8.4 μmol ofrac-dimethylmethylenebis(4,5-benzo-1-indenyl)zirconium dichloride and0.84 mmol of triisobutyl aluminum dissolved therein, was added to theautoclave. Polymerization (the first polymerization step) was carriedout for 45 minutes while maintaining the internal temperature at 70° C.and the pressure at 0.25 MPa. At this stage, the amount of ethyleneconsumed was about 100 l in a standard state. A part of thepolymerization solution was sampled, and a polymer sample (polymer 1-A)of the first polymerization step was obtained by precipitation frommethanol. Ethylene was introduced rapidly, and the internal pressure wasbrought to 1.1 MPa in 25 minutes. By the increase of the ethylenepressure, polymerization was accelerated, whereby the internaltemperature rose from 70° C. up to 80° C. While maintaining the pressureat 1.1 MPa, polymerization was carried out for 70 minutes (the secondpolymerization step).

After completion of the polymerization, the obtained polymer solutionwas introduced in small portions into a large amount of a methanolsolution which was vigorously stirred, to recover the polymer. Thispolymer was dried in air at room temperature for one day, and then,dried under vacuum at 80° C. until change in weight was no longer,observed. 805 g of the polymer (polymer 1-C) was obtained.

The polymerization conditions in the respective examples were summarizedin Table 1.

The analytical results of the polymers obtained in the respectiveExamples and Comparative Examples are shown in Table 2.

TABLE 1 Polymerization Conditions First polymerization step (main chainpolymerization step) Et Polymerization Et Polymerization Conversion (%)in Catalyst MAO St DVB Toluene pressure temperature consumption timefirst polymerization Ex. μmol mmol ml ml ml MPa ° C. amount l (min.)step % Ex. 1 8.4 P; 21 400 1.0 4400 0.25 70 About 100  64 38 Ex. 2 8.4P; 21 400 1.0 4400 0.25 70 About 150  96 45 Ex. 3 8.4 P; 21 400 1.0 44000.25 70 About 200 150 60 Second polymerization step (cross chainpolymerization step) Et St conversion pres- Et (%) in second Final Stsure Polymerization consumption Polymerization polymerization conversionEx. MPa temperture ° C. amount l time (min.) step Note 1 (%) Ex. 1 1.170-80 About 300 77 56 73 Ex. 2 1.1 70-80 About 370 81 56 75 Ex. 3 1.170-90 About 260 65 22 68 Note 1: St conversion (%) in secondpolymerization step; ratio of the amount of styrene monomer converted topolymer during second polymerization step, to the amount of styrenemonomer present in polymerization solution at the initiation of secondpolymerization step. (A styrene monomer amount in a polymerizationsolution present at the initiation of second polymerization step wasdetermined by taking a part of a polymer solution obtained in first #polymerization step and measuring weight balance from its polymerconcentration and composition.) Note 2: Final St conversion (%); ratioof the amount of styrene monomer finally converted to polymer throughfirst and second polymerization steps, to the amount of styrene monomerinitially charged.

TABLE 2 Polymerization Results Glass Heat of Styrene transition crystalYield content temperature Melting fusion Ex. Polymers 1) g mol % Mw/10⁴Mw/Mn ° C. point ° C. J/g Ex. 1 1-A 260 23.0 16.0 2.4 −18 None — 1-B 5457.6 — — — — — 1-C 805 11.6 (15.7) (4.7) −20 103 35 Ex. 2 2-A 352 19.119.9 2.8 −18  48 17 2-B 543 6.5 — — — — — 2-C 895 10.7 (17.9) (4.8) −20106 34 Ex. 3 3-A 470 18.9 19.4 2.9 −20  53 23 3-B 393 2.3 — — — — — 3-C863 9.8 (21.7) (4.1) −21 109 83 A value of polymer A was determined froma polymer obtained by sampling a part of a polymerization solution atthe end of first polymerization step. Polymer B (1-B, 2-B and 3-B) is acopolymer obtained in second polymerization step (cross chainpolymerization step) (including a copolymer component formed duringraising an ethylene pressure). Polymer C (1-C, 2-C and 3-C) is across-copolymer finally obtained through the first and secondpolymerization steps. Yield and styrene content of polymer B weredetermined from weight balance of polymer A and polymer C. Styrenecontent of polymer B is an average styrene content of a copolymerobtained in second polymerization step. Mw or Mw/Mn in the brackets ( )is a reference value.

In Table 2, in addition to the polymer (1-A) obtained in the firstpolymerization step and the cross-copolymer i.e. the polymer (1-C)finally obtained through the second polymerization step, the weight andthe composition of the polymer (1-B) polymerized in the secondpolymerization step are also shown as determined from weight balance.

EXAMPLES 2 AND 3

Under the conditions shown in Table 1, polymerization and post treatmentwere carried out in the same manner as in Example 1. By the gaschromatography analysis of the polymerization solution withdrawn uponcompletion of the first polymerization step, the amount ofdivinylbenzene remaining in the polymerization solution was obtained,and the amount of divinylbenzene consumed in the first polymerizationstep was obtained. From the value, the divinylbenzene content in thecopolymer obtained in each first polymerization step was obtained,whereby it was about 0.04 mol % with polymer 1-A, about 0.04 mol % withpolymer 2-A and about 0.07 mol % with polymer 3-A.

The structural index λ of the cross-copolymer obtained in each Exampleand the isotactic diad index m of the styrene unit/ethylene unitalternating structure, were obtained in accordance with the aboveformulae (i) and (ii), respectively. λ values and m values obtained inExamples are shown in Table 3, and other results of measurements areshown in Tables 4 and 5.

TABLE 3 St content Examples mol % λ value m value Example 1 1-A 23.016 >0.95 Example 1 1-C 11.6 10 >0.95 Example 2 2-A 19.1 14 >0.95 Example2 2-C 10.7 8 >0.95 Example 3 3-A 19.1 15 >0.95 Example 3 3-C 9.8 8 >0.95

TABLE 4 Example 1 Example 2 Example 3 Kind of polymer 1-C 2-C 3-CBreaking 517 500 500 elongation (%) Yield Yield point Yield point Yieldpoint strength was not was not was not (MPa) observed observed observedBreaking 34.9 35.8 31.2 strength (MPa) Elastic 29.5 29.2 38 modulus intension (MPa) 100% modulus 6.0 5.3 6.7 (MPa) 300% modulus 10.0 9.7 9.8(MPa) Hardness 88 88 90 (Shore A) Hardness 39 36 39 (Shore D) Totallight 80 83 81 transmittance (%) Haze (%) 15 13 17 Vicat 96 95 95softening point (° C.) MFR (g/10 min.) 0.13 0.06 Unmeasured 200° C.

TABLE 5 Gel content of polymer Example 1 (1-A) 0% Example 1 (1-C) 0%Example 2 (2-A) 0% Example 2 (2-C) 0% Example 3 (3-A) 0% Example 3 (3-C)0%

In the Table, “0%” means “less than 0.1%”.

Comparative Examples 1 to 6

Ethylene/styrene copolymers having various styrene contents obtained bypolymerization carried out in the method disclosed in EP-0872492A2 andJP-A-11-130808 usingrac-dimethylmethylenebis(4,5-benzo-1-indenyl)zirconium dichloride as acatalyst and methyl alumoxane (MAO) as a cocatalyst, are shown in Table6

TABLE 6 Glass St Melting transition content Mw/ Mw/ point point mol %10⁴ Mn ° C. ° C. Comparative R-1 5 18.5 2.1 103 −25 Example 1Comparative R-2 7 18.0 2.0 93 −28 Example 2 Comparative R-3 11 16.0 1.979 −22 Example 3 Comparative R-4 13 22.7 2.0 68 −23 Example 4Comparative R-5 17 17.5 2.0 63 −22 Example 5 Comparative R-6 21 18.5 2.0Unmeasured Unmeasured Example 6

Comparative Example 7

Using a Brabender Plasti-Corder (PLE331 Model, manufactured by BrabenderCompany), 25 g of each of copolymers R-2 and R-6 was melted and thenkneading (external temperature: 180° C., rotational speed: 60 RPM, time:10 minutes) was carried out to obtain a composition. The obtainedethylene/styrene copolymer composition was molded by the above-mentionedpress molding to obtain a sheet of 1 mm in thickness, and evaluation ofvarious physical properties was carried out. In Tables 7 and 8, the testresults of the physical properties of the polymers of ComparativeExamples and various polymers obtained, are shown.

TABLE 7 Comp. Comp. Comp. Comp. Comp. Comp. Comp. Ex. 1 Ex. 2 Ex. 3 Ex.4 Ex. 5 Ex. 6 Ex. 7 Kind of polymer R-1 R-2 R-3 R-4 R-5 R-6 R-2 + R-6 5mol % 7 mol % 11 mol % 13 mol % 17 mol % 21 mol % Breaking 630 533 450440 500 1333 533 elongation (%) Yield strength Yield Yield Yield YieldYield Yield Yield (MPa) point point point point point point point wasnot was not was not was not was not was not was not observed observedobserved observed observed observed observed Breaking 34.0 50.0 45.036.0 48.0 7.6 34.3 strength (MPa) Elastic modulus 66.0 34.0 18.0 17.09.0 3.1 14.5 in tension (MPa) 100% Modulus 9.0 6.0 5.0 4.0 3.0 1.3 3.8(MPa) 300% Modulus 11.0 10.0 9.0 8.0 6.0 1.6 6.9 (MPa) Hardness 96 94 8482 78 63 82 (Shore A) Hardness 47 44 31 30 25 19 31 (Shore D) Totallight 80 85 82 86 Unmeasured 84 73 transmittance (%) Haze (%) 20 13 2212 Unmeasured 12 47 Vicat softening 99 94 77 70 61 40 76 point (° C.)

TABLE 8 Comparative Example 4 Example 5 Example 6 Example 7 Example 8Cross-copolymer 2-C 2-C 2-C 2-C —  100 parts  100 parts  100 parts  100parts Et-St copolymer — — — — R-3  100 parts Stabilizer  0.3 part   0.3part   0.3 part   0.3 part   0.3 part  (Irganox1010) Plasticizer — —  20 parts   50 parts — (naphthene type oil) NS-100 Plasticizer —   50parts — — — (paraffin type oil) PW-380 Poly- — — —   50 parts —propylene K-7714 Breaking 540 650 680 670 Unmeasured elongation (%)Breaking 30 10 17 9 Unmeasured strength (MPa) Hardness 88 73 79 87Unmeasured (Shore A) C-set (%) 67 54 59 65 93

It is evident that the cross-copolymerizedstyrene/ethylene/divinylbenzene copolymers of the Examples of thepresent invention have high mechanical strengths, high melting points,Vicat Softening points and transparency. When the physical propertiesare compared with ethylene/styrene copolymers having the samecompositions (styrene contents), they show higher melting points andVicat softening points and show equivalent transparency. The meltingpoints and the Vidat softening points of the cross-copolymers of theExamples of the present invention have values substantially equal to orhigher than ethylene/styrene copolymers having the same styrene contentsas the cross chain component polymerized in the second polymerizationstep (the crossing step). Namely, cross-copolymer (1-C) obtained inExample 1 has an average styrene content of 11.6 mol %, and,nevertheless, its melting point and its vicat softening point aresubstantially equal to or higher than the ethylene/styrene copolymer(R-1 or R-2) having a styrene content of 5 or 7 mol %. Whereas, shorehardness A and D and the elastic modulus in tension are lower than R-1or R-2, which is considered to be attributable to the effects of themain chain component (the component obtained in the first polymerizationstep) having a high styrene content of the cross-copolymer.

FIG. 3 shows the relation between the styrene content and the DSCmelting point of the cross-copolymers obtained in the Examples of thepresent invention and the ethylene/styrene copolymers of the ComparativeExamples.

Further, FIG. 4 shows a relation between the styrene content and theVicat softening point of the cross-copolymers-obtained in the Examplesof the present invention, the ethylene/styrene copolymers of ComparativeExamples and the blend product obtained by mixing the ethylene/styrenecopolymers of Comparative Examples by a Brabender. It is evident thatthe cross-copolymers of the Examples of the present invention havehigher Vicat softening points as compared with the ethylene/styrenecopolymers or the blend product of the ethylene/styrene copolymers. Theblend products obtained by mixing the ethylene/styrene copolymers ofComparative Examples by a Brabender, in FIG. 4, are a blend product ofR-2 and R-6 in Table 7 (weight ratio of 1:1, average styrene content: 13mol %), a blend product of R-2 and R-4 (weight ratio of 1:1, averagestyrene content: 11 mol %), and a blend product of R-4 and R-6 (weightratio of 1:1, average styrene content: 17 mol %).

As a Comparative Test, ethylene/styrene copolymers (R-2 and R-6) havingstyrene contents close to the main chain and the cross chain ofcross-copolymer (1-C) were kneaded in a weight ratio of 1:1 to obtain acomposition. The obtained composition was opaque as shown in the table.It is evident that in the case of a composition of ethylene/styrenecopolymers substantially different in their compositions (for example,different in the styrene content by at least 10 mol %), the transparencydeteriorates, as the compatibility is poor.

Further, the cross-copolymerized styrene/ethylene/diene copolymersobtained in the Examples of the present invention show goodprocessabilities (MFR, the MFR measured under a load of 5 kg at 200° C.is at least 0.02 g/10 min.).

The gel content of the cross-copolymer was measured in accordance withASTM D-2765-84. Namely, accurately weighed 10 g of a polymer (a moldedproduct having a diameter of about 1 mm and a length of about 3 mm) wasenclosed in a 100 mesh stainless steel net bag and accurately weighed.This was extracted in boiling xylene for about 5 hours, whereupon thenet bag was recovered and dried under vacuum at 90° C. for at least 10hours. After cooling sufficiently, the net bag was accurately weighed,and the amount of the polymer gel was calculated by the followingformula.Gel amount=weight of polymer remaining on the net bag/weight of initialpolymer×100

The results are shown in Table 6. In each case, the gel content was 0%(measurable lower limit: 0.1 weight %), which shows that thecross-copolymers of the present invention have extremely low gelcontents and crosslinking degrees.

This is explained in such a way that the coordination polymerizationcatalyst used in the Examples of the present invention is capable ofcopolymerizing dienes at high efficiency, and crossing will adequatelyproceed at a very low level of the amount of dienes used. It isconsidered that the amount and the concentration of the diene remainingin the polymerization solution are sufficiently low, wherebycrosslinking at the diene units of the copolymer during thepolymerization can be suppressed to an extremely low level, wherebyformation of the gel component will be suppressed.

Also in the crossing step, formation of the gel component is suppressedas the amount and concentration of the remaining diene are low.

By the X-ray diffraction, a crystal structure derived from ethylenechains was confirmed with the cross-copolymers of the Examples of thepresent invention i.e. polymer (1-C.), polymer (2-C) and polymer (3-C).The X-ray diffraction diagram of polymer (1-C) is shown in FIG. 5. Peaksattributable to the polyethylene crystal structure are clearly observedin the vicinity of 2θ=21° or 24°. Amorphous scattering peaks anddiffraction peaks are subjected to peak separation to obtain peak areas(peak integrated intensities), and the crystallinity was obtained by thefollowing formula.Crystallinity (%)=100×(sum of integrated intensities of crystallinediffraction peaks)/(sum of integrated intensities of crystallinediffraction peaks and amorphous scattering peaks)

As a result, the crystallinity of cross-copolymer (1-C) was 30%.

As a Comparative Example, the X-ray diffraction diagram ofethylene/styrene copolymer (R-4) having substantially the same styrenecontent, is shown in FIG. 6. As compared with the cross-copolymer, thepeak intensity attributable to the polyethylene crystal structure islow, and its crystallinity was 14%.

The brittle temperatures of the cross-copolymers of the Examples of thepresent invention were measured in accordance with JIS K-6723 andK-7216. As a result, cross-copolymers 1-C and 2-C both showed brittletemperatures of not higher than −60° C. A transparent soft polyvinylchloride compound (Vinikon S2100-50, manufactured by Denki Kagaku K. K.)showed a brittle temperature of substantially −25° C.

FIGS. 7 and 8 show the viscoelasticity spectra (measured at 1 Hz) of thefilms of the cross-copolymers obtained in Examples 1 and 2. Further,FIG. 9 shows the viscoelasticity spectrum of the ethylene/styrenecopolymer composition of a Comparative Example. E′ (storage elasticmodulus) of the cross-copolymer of the Example of the present inventionshows a high value especially at a temperature of at least 50° C., ascompared with the ethylene/styrene copolymer having the same styrenecontent. Further, E′ shows a value higher than 10⁶ Pa at 100° C., andthe temperature at which it lowers to 10⁶ Pa;, is about 105° C., whichis high as compared with about 80° C. of the ethylene/styrene copolymer,thus indicating that it has high heat resistance.

It is evident that the cross-copolymer of the Example of the presentinvention has a tan δ peak component of from 0.05 to 0.8 at about roomtemperature (0° C. or 25° C). Further, it has a wide range of tan δpeaks from about −30° C. to about 50° C. Specifically, the tan δ valueis at least 0.1 within a temperature range of from −10° C. to 50° C.

The copolymer of the present invention or a film made of the copolymerof the present invention has such characteristics of E′ and tan δ value,and flexibility or softness such that hardness A is from 60 to 90 and/orthe elastic modulus in tension is from 10 MPa to 40 MPa.

Measurement of C-set

Using Brabender Plasti-Corder (PLE 331 model, manufactured by BrabenderCompany), the polymer was melted and then kneaded in a blend as shown inTable 8 at 200° C. at 60 rpm for 10 minutes to obtain a sample. Thesample was press-molded, and the physical properties were measured.Further, in accordance with JIS K6262, a high temperature compressionpermanent deformation (C-set) after heat treatment under pressure at 70°C. for 24 hours, was measured. The cross-copolymer of the Example of thepresent invention has a low C-set value (67%). This indicates agood-high temperature elastic recovery of the cross-copolymer of theepresent invention. Further, it is also possible to improve the C-setvalue and to lower the hardness, by blending it with a plasticizer.Further, a composition with a polypropylene showed no deformation byheat treatment at 120° C. for 2 hours (a dumbbell was hanged in a gearoven and the deformation was observed), and thus showed high heatsoftening resistance.

On the other hand, the C-set value of the ethylene/styrene copolymer ofthe Comparative Example was 93%.

Divinylbenzene

The divinylbenzene (a mixed product of m-isomer and p-isomer) used inthe following Examples 8 to 10, was manufactured by Aldrich Company(purity as divinylbenzene: 80%, a mixture of m-isomer and p-isomer,weight ratio of m-isomer:p-isomer=70:30, accordingly, the isomer purityof m-divinylbenzene is 70 weight %). In the following polymerization,when 1 ml (5.5 mmol as divinylbenzene) was employed per 400 ml ofstyrene, the amount of divinylbenzene corresponds to 1/640 of the amountof styrene by molar ratio.

Further, in the following Examples 11 to 13, m-divinylbenzene (isomerpurity: at least 97%) manufactured by Asahi Kasei Fine Chem, wasemployed. In this case, the isomers purity is the proportion ofm-divinylbenzene among o-, m- and p-divinylbenzene isomers.

EXAMPLE 8

Preparation of a Cross-copolymerized Ethylene/styrene/divinylbenzeneCopolymer

Using rac-dimethylmethylenebiis (4,5-benzo-1-indenyl)zirconiumdichloride as a catalyst, the preparation was carried out, as follows.

Polymerization was carried out by means of an autoclave having acapacity of 10 l and equipped with a stirrer and a jacket for heatingand cooling.

4400 ml of toluene, 400 ml of styrene and 2.0 ml of divinylbenzenemanufactured by Aldrich Company were charged and heated and stirred atan internal temperature of 70° C. About 200 l of nitrogen was bubbled topurge the interior of the system and the polymerization solution. 8.4mmol of triisobutyl aluminum and 21 mmol, based on Al, of methylalumoxane (PMAO-3A, manufactured by TOSOH AKZO K. K.) were added, andethylene was immediately introduced. After the pressure was stabilizedat 0.25 MPa (1.5 kg/cm²G), from a catalyst tank installed above theautoclave, about 50 ml of a toluene solution having 8.4 μmol ofrac-dimethylmethylenebis(4,5-benzo-1-indenyl)zirconium dichloride and0.84 mmol of triisobutyl aluminum dissolved therein, was added to theautoclave. Polymerization (the first polymerization step) was carriedout for 24 minutes while maintaining the internal temperature at 70° C.and the pressure at 0.25 MPa. At this stage, the flow volume of ethylenewas about 100 l in a standard state. At the same time as heating of thepolymerization solution was initiated, a part of the polymerizationsolution was sampled, and a polymer sample (8-A) of the firstpolymerization step was obtained by precipitation from methanol.Ethylene was introduced rapidly, and the internal pressure was broughtto 1.1 MPa in 12 minutes. In the second polymerization step, thepolymerization temperature was maintained within an internal temperaturerange of from 97° C. to 105° C. The second polymerization step wascarried out for a total of 18 minutes while maintaining the pressure at1.1 MPa.

After completion of the polymerization, the obtained polymer solutionwas introduced in small portions into a large amount of a methanolsolution which was vigorously stirred, to recover the polymer. Thispolymer was dried in air at room temperature for one day, and then,dried under vacuum at 80° C. until change in weight was no longerobserved. 784 g of the polymer (8-C) was obtained.

The polymerization conditions in the respective Examples were summarizedin Table 9. The analytical results of the polymers obtained in therespective Examples are shown in Table 10.

TABLE 9 Polymerization Conditions First polymerization step (main chainpolymerization step) St conversion (%) in DVB Et PolymerizationPolymerization first Catalyst MAO St ml Toluene pressure temperature Etflow time polymerization Ex. μmol mmol* ml (mmol) ml MPa ° C. volume l(min.) step % Ex. 8 8.4 P; 21 400 2.0 ml Note 1 4400 0.25 70 About 10024 40 (11 mmol) Ex. 9 8.4 P; 16.8 400 0.5 ml Note 1 4400 0.25 70-80About 100 57 35 (2.8 mmol) Ex. 10 21 P; 21 800 1.0 ml Note 1 4000 0.1370 About 70 120 62 (5.5 mmol) Ex. 11 8.4 P; 16.8 400 0.73 g Note 2 44000.25 70-80 About 150 44 53 (5.4 mmol) Ex. 12 8.4 P; 16.8 400 0.73 g Note2 4400 0.25 70-80 About 200 91 65 (5.4 mmol) Ex. 13 8.4 P; 21 400 0.73 gNote 2 4400 0.25 80-85 About 250 117 72 (5.4 mmol) Second polymerizationstep (cross chain polymerization step) Final St Polymerization Etconsumption Polymerization conversion (%) Ex. Et pressure MPatemperature ° C. amount l time (min.) Note 3 Ex. 8 1.1 97-105 About 20018 66 Ex. 9 1.1 85-102 About 300 52 60 Ex. 10 1.1 70-83  About 250 60 82Ex. 11 1.1 92-104 About 270 52 79 Ex. 12 1.1 91-103 About 220 79 79 Ex.13 1.1 80-95  About 170 28 89 P; PMAO (manufactured by Toso Fine Chem)Note 1: Divinylbenzene manufactured by Aldrich Company, divinylbenzenepurity: 80% (mixture of m-isomer and p-isomer, weight ratio of m-isomer:p-isomer = 70:30, isomer purity of m-divinylbenzene: 70%) Note 2:Metadivinylbenzene manufactured by Asahi Kasei Fine Chem (m-DVB, isomerpurity of m-divinylbenzene: at least 97%) Note 3: Final St conversion(%); ratio of the amount of styrene monomer finally converted to polymerthrough first and second polymerization steps, to the amount of styrenemonomer initially charged.

TABLE 10 Polymerization Results Glass Heat of Styrene transition crystalYield content temperature Melting fusion Ex. Polymers 1) g mol % Mw/10⁴Mw/Mn ° C. point ° C. J/g Ex. 8 8-A 286 22.1 17.8 2.5 −20  42  4 8-B 4985.8 — — — — — 8-C 784 10.6 (17.4) (2.9) −21  97 57 Ex. 9 9-A 250 21.315.5 2.2 −19  44  5 9-B 635 4.5 — — — — — 9-C 885 8.2 UnmeasurableUnmeasurable −19 105 63 Ex. 10 10-A 610 42.9 14.9 2.4   17   92*  19*10-B 623 7.7 — — — — — 10-C 1233 20.1 (12.7) (2.5) −23, −16  80 30 Ex.11 11-A 405 19.6 17.3 2.5 −19  47  8 11-B 565 5.1 — — — — — 11-C 97010.2 Unmeasurable Unmeasurable −20 103 58 Ex. 12 12-A 530 17.8 20.2 2.8−20  51 10 12-B 447 3.4 — — — — — 12-C 977 10.1 UnmeasurableUnmeasurable −21 109 53 Ex. 13 13-A 651 15.4 17.3 2.8 −22  60 11 13-B326 6.2 — — — — — 13-C 977 11.9 Unmeasurable Unmeasurable −21 112 49 Avalue of polymer A (such as 8-A) was determined from a polymer obtainedby sampling a part of a polymerization solution at the end of firstpolymerization step. Polymer B (such as 8-B) is a copolymer obtained insecond polymerization step (cross chain polymerization step) (includinga copolymer component formed during raising an ethylene pressure).Polymer C (such as 8-C) is a cross-copolymer finally obtained throughthe first and second polymerization steps. Yield and styrene content ofpolymer B were determined from weight balance of polymer A and polymerC. *DSC measurement, results of 1st run. Mw or Mw/Mn in the brackets ( )is a reference value.

In Table 10, in addition to the polymer (such as 8-A) obtained in thefirst polymerization step and the cross-copolymer i.e. the polymer (suchas 8-C) finally obtained through the second polymerization step, theweight and the composition of the polymer (such as 8-B) polymerized inthe second polymerization step are also shown as determined from weightbalance.

EXAMPLES 9 AND 10

Under the conditions shown in Table 9, polymerization and post treatmentwere carried out in the same manner as in Example 8.

EXAMPLES 11 TO 13

Under the conditions shown in Table 9, polymerization and post treatmentwere carried out in the same manner as in Example 8. However, thedivinylbenzene employed was m-divinylbenzene (isomer purity: at least97%) manufactured by Asahi Kasei Fine Chem.

The cross-copolymerization conditions in these Examples satisfy thepreferred conditions for obtaining cross-copolymers having goodmoldability, as follows.

Example 8 satisfies a condition that a) in the first and/or secondpolymerization step, the polymerization temperature is substantiallyalways at least 80° C., preferably at least 85° C. and at most 160° C.during the polymerization.

Example 9 satisfies a condition that a) in the first and/or secondpolymerization step, the polymerization temperature is substantiallyalways at least 80° C., preferably at least 85° C. and at most 160° C.,during the polymerization.

Example 10 satisfies a condition that b) the aromatic vinyl compoundcontent of the polymer obtained in the first polymerization step is atleast 30 mol %, and its weight average molecular weight is at most250,000.

Examples 11 to 13 satisfy conditions that a) in the first and/or secondpolymerization step, the polymerization temperature is substantiallyalways at least 80° C., preferably at least 85° C. and at most 160° C.,during the polymerization, and c) the diene to be employed ism-divinylbenzene having an isomer purity of at least 80 weight %,preferably at least 90 weight %.

By the gas chromatography analysis of the polymerization solutionwithdrawn upon completion of the first polymerization step, the amountof divinylbenzene remaining in the polymerization solution was obtained,and the amount of divinylbenzene consumed in the first polymerizationstep was obtained. From the value, the obtained in each Example and theisotactic diad index m of the styrene unit/ethylene unit alternatingstructure, were obtained in accordance with the above formulae (i) and(ii), respectively. λ values of 8-A, 9-A, 11-A, 12-A and 13-A obtainedin the first polymerization step were within a range of from 12 to 20,and λ value of 10-A was 39.

λ values of the cross-copolymers 8-C, 9-C, 11-C, 12-C and 13-C obtainedthrough the second polymerization step were within a range of from 7 to15, and λ value of 10-C was 24.

m value of each polymer was at least 0.95. The result of measurement ofphysical properties of the obtained polymers are shown in Table 11.

TABLE 11 Example 8 Example 9 Example 11 Example 12 Example 13 Kind of8-C 9-C 11-C 12-C 13-C polymer Breaking 510 633 483 443 520 elongation(%) Yield strength Yield point Yield point Yield point Yield point Yieldpoint (MPa) was not was not was not was not was not observed observedobserved observed observed Breaking 26.1 20.9 25.0 22.7 27.0 strength(MPa) Elastic 20.2 35.0 24.2 29.1 17.2 modulus in tension (MPa) 100%modulus 5.0 6.0 5.2 5.7 4.0 (MPa) 300% modulus 8.9 7.4 9.4 9.4 8.6 (MPa)Hardness 90 95 88 88 84 (Shore A) Hardness 35 42 37 37 32 (Shore D)Total light 81 73 83 85 83 transmittance (%) Haze (%) 11 18 11 11 12

It is evident that the cross-copolymerizedstyrene/ethylene/divinylbenzene copolymers of the Examples of thepresent invention have high mechanical strengths, high melting pointsand transparency. When the physical properties are compared withethylene/styrene copolymers having the same compositions (styrenecontents), they show higher melting points and show transparencyequivalent to or higher than the ethylene/styrene copolymers. Themelting points of the cross-copolymers of the Examples of the presentinvention have values substantially equal to or higher thanethylene/styrene copolymers having the same styrene contents as thecross chain component polymerized in the second polymerization step (thecrossing step). Namely, cross-copolymer (8-C). obtained in Example 8 hasan average styrene content of 10.6 mol %, and, nevertheless, its meltingpoint is significantly higher than the ethylene/styrene copolymer havingthe same styrene content. Whereas, shore hardness A and D and theelastic modulus in tension of the cross-copolymer are substantially thesame as the ethylene/styrene copolymer having the same styrene content,thus showing that the cross-copolymer has both heat resistance andsoftness. This is considered to be attributable to the effects of themain chain component (the component obtained in the first polymerizationstep) having a high styrene content and low crystallinity and the crosschain component (the component obtained in the second polymerizationstep) having a low styrene content and high crystallinity.

FIG. 9 shows the relation between the styrene content and the DSCmelting point of the cross-copolymers obtained in Examples 8 to 13 ofthe present invention and the ethylene/styrene copolymers of theComparative Examples.

The cross-copolymerized styrene/ethylene/diene copolymers obtained inExamples of the present invention, show good processability (ER; i.e.MFR as measured under a load of 5 kg at 230° C. being at least 1.0 g/10min and at most 50 g/10 min) (Table 12)

In general, there is a tendency that the processability (MFR) decreasesas the final conversion of styrene (the conversion of the aromatic vinylcompound monomer species throughout all polymerization steps) increases.Such a decrease in the mold processability is observed particularlydistinctly in a case where the aromatic vinyl compound content of thepolymer obtained in the first polymerization step is less than 30 mol %.However, especially in a case whereas a diene, m-divinylbenzene havingan isomer purity of at least 80 weight %, preferably at least 90 weight% (Examples 11, 12 and 13) is used, even if a cross-copolymer isproduced under such a condition that the final conversion of styrene (anaromatic vinyl compound) is at least 70%, the obtainable cross-copolymerhas a characteristic of showing good processability (MFR, i.e. MFR asmeasured under a load of 5 kg at 230° C. being at least 1.0 g/10 min.and at most 50 g/10 min.). It is preferred to employ m-divinylbenzenefor the production of a cross-copolymer from such a viewpoint that goodmold processability (M) is obtainable while maintaining various physicalproperties such as heat resistance and transparency even under such acondition.

TABLE 12 MFR Ex. 8 Ex. 9 Ex. 10 Ex. 11 Ex. 12 Ex. 13 (g/10 min.) 8-C 9-C10-C 11-C 12-C 13-C 230° C., load 1.5 2.3 1.9 1.2 1.2 1.1 5 kg 230° C.,load 6.7 8.8 5.9 5.2 6.0 4.0 10 kg

The gel contents of the cross-copolymers obtained in Examples 8 to 13were measured in accordance with ASTM D-2765-84. In the cross-copolymersin all of such Examples, the gel content was 0 weight % (the lower limitfor measurement: 0.1 weight %), whereby it is evident that thecross-copolymers of the present invention have extremely low gelcontents or crosslinking degrees.

By the X-ray diffraction, a crystal structure derived from ethylenechains was confirmed with the cross-copolymers of Examples 8 to 13 ofthe present invention.

The brittle temperatures of the cross-copolymers in Examples of thepresent invention were measured in accordance with JIS K-6723 and K-7216As a result, each of cross-copolymers 8-C, 9-C, 11-C, 12-C and 13-C,showed a brittle temperature of not higher than −60° C.

FIG. 11 shows a transmission, electron microscopic (TEM) photograph ofthe cross-copolymer obtained in Example 8 and FIG. 12 shows a TEMphotograph of the ethylene/styrene copolymer composition of ComparativeExample 7.

In the case of the ethylene/styrene copolymer composition, copolymerportions (white portions) having a low styrene content and copolymerportions (black portions) having a relatively high styrene content arephase-separated in sizes of a few microns, and is crystalline lamella(white needle crystal) is present only inside of the copolymer regionshaving a low styrene content. This result indicates low compatibility ofethylene/styrene copolymers having different compositions from eachother.

Whereas, in the cross-copolymer, the portions (white portions) having alow styrene content and the portions (black portions) having arelatively high styrene content are both finely distributed in sizes ofabout 0.1 μm or smaller. Further, crystalline lamella (white needlecrystal) is present substantially at the interface, and it is alsoobserved in high styrene regions, and thus it takes a specific structurebridging both phases.

EXAMPLES 14 TO 19 AND COMPARATIVE EXAMPLE 9

In accordance with the blend ratios shown in Table 13, copolymercompositions were obtained, and by the following method, C-set and heatresistance were measured.

Measurement of C-set

Using Brabender Plasti-Corder (PLE 331 model, manufactured by BrabenderCompany), the polymer was melted and then kneaded in a blend ratio asshown in Table 13 at 200° C. at 60 rpm for 10 minutes to obtain asample. The sample was press-molded, and the physical properties weremeasured. Further, in accordance with JIS K6262, a high temperaturecompression permanent deformation (C-set) after heat treatment underpressure at 70° C. for 24 hours, was measured (Table 13). The heatresistance was evaluated by heat treatment of a dumbbell obtained bypress molding (the dumbbell was hanged in a gear oven at 120° C. for twohours, and the deformation was observed).

The cross-copolymers of Examples of the present invention have low C-setvalues (65%). This indicates a good elastic recovery under a hightemperature condition of the cross-copolymers of the present invention.Further, the heat resistance is also relatively good. Further, it ispossible to improve the C-set value or to lower the hardness by blendingthe copolymer with a plasticizer.

On the other hand, the C-set value of the composition (ComparativeExample 9) comprising ethylene/styrene copolymers having differentcompositions, is poor at 100%, and the heat resistance is also poor.

The composition comprising the cross-copolymer, a polyolefin(polyethylene) and a plasticizer showed a good C-set value and high heatresistance (Examples 18 and 19).

TABLE 13 Ex. 14 Ex. 15 Ex. 16 Ex. 17 Ex. 18 Ex. 19 Comp. Ex. 9 BlendCross-copolymer 8-C 9-C 11-C 12-C 12-C 12-C — ratio  100 parts  100parts  100 parts  100 parts  100 parts  100 parts Et-St copolymer — — —— R-1:50 parts + R-6:50 parts High density — — — —   50 parts   20 parts— polyethylene 7000 F Plasticizer NS-100 — — — —   50 parts   50 parts —(Naphthene type oil) Physical Breaking — — — — 780 720 — propertyelongation (%) Breaking strength — — — — 12.6 10.0 — (MPa) Hardness(Shore A) — — — — 93 87 — Stabilizer  0.3 part   0.3 part   0.3 part  0.3 part   0.3 part   0.3 part   0.3 part  (Irganox 1010) C-set (%) 6965 65 68 49 53 100 Heat resistance ◯ ◯ ◯ ◯ ⊚ ⊚ X (120° C., 2 hours) ◯:Not melted, but shrinkage observed. ⊚: Not melted, and no change inshape observed. X: Melted and dropped.Industrial Applicability

According to the present invention, a cross-copolymerizedolefin/styrene/diene copolymer excellent in mechanical properties, hightemperature characteristics, compatibility and transparency, andindustrially excellent processes for the production of such across-copolymer and its composition, are presented.

The entire disclosures of Japanese Patent Application No. 11-258618filed on Sep. 13, 1999, Japanese Patent Application No. 2000-184053filed on Jun. 20, 2000, Japanese Patent Application No. 2001-044715filed on Feb. 21, 2001, and Japanese Patent Application No. 2001-221247filed on Jul. 23, 2001 including specifications, claims, drawings andsummaries are incorporated herein by reference in their entireties.

1. An olefin/aromatic vinyl compound/divinylbenzene copolymer having anaromatic vinyl compound content of from 0 mol % to 96 mol %, a dienecontent of from 0.0001 mol % to 3 mol % and the rest being an olefin,obtained by copolymerizing m-divinylbenzene having an isomer purity ofat least 80 weight %, an olefin and an aromatic vinyl compound.
 2. Theolefin/aromatic vinyl compound/divinylbenzene copolymer according toclaim 1, wherein the m-divinylbenzene has an isomer purity of at least90 weight %.
 3. A process for producing the olefin/aromatic vinylcompound/divinylbenzene copolymer of claim 1, the process comprisingcopolymerizing m-divinylbenzene having an isomer purity of at least 80weight %, an olefin and an aromatic vinyl compound in the presence of asingle site coordination polymerization catalyst.
 4. Across-copolymerized olefin/aromatic vinyl compound/diene copolymer, across-linked polymer, a resin composition, or material made from orcomprising the olefin/aromatic vinyl compound/divinylbenzene copolymerof claim 1.